High pressure low density polyethylene resins with improved optical properties produced through use of highly active chain transfer agents

ABSTRACT

Disclosed is an ethylene-based polymer with a density from about 0.90 to about 0.94 in grams per cubic centimeter, with a molecular weight distribution (M w /M n ) from about 2 to about 30, a melt index (I 2 ) from about 0.1 to about 50 grams per 10 minutes, and further comprising sulfur from about 5 to about 4000 parts per million. The amount of sulfur is also determined based upon the total weight of the ethylene-based polymer. Also disclosed is process for making an ethylene-based polymer which includes the steps of splitting a process fluid for delivery into a tubular reactor; feeding an upstream process feed stream into a first reaction zone and at least one downstream process feed stream into at least one other reaction zone, where the process fluid has an average velocity of at least 10 meters per second; and initiating a free-radical polymerization reaction.

CROSS-REFERENCE TO RELATED PATENT APPLICATIONS

This application claims priority from U.S. Provisional Application Ser.No. 61/103,374, filed Oct. 7, 2008 (Attorney Docket No. 67403). Forpurposes of United States patent practice, the contents of thisapplication is herein incorporated by reference in its entirety.

FIELD OF THE INVENTION

This invention relates to compositions and processes for forming lowdensity ethylene-based polymers such as high pressure, low densitypolyethylene (LDPE) resins.

BACKGROUND OF THE INVENTION

LDPE has been produced in autoclave reactors, tubular reactors, andcombinations thereof. Each type of reactor has its advantages anddisadvantages, but economics and product design drive the need forimprovements. The operation of and type(s) of reactor(s) employed candramatically affect the physical properties of the resulting LDPE. Suchimprovements are desired for applications such as blown and cast film,where especially good optical properties are desired.

High pressure, low density ethylene-based polymers have a density in arange of about 0.91 to about 0.94 g/cm³. Low density ethylene-basedpolymers typically have random branching structures that contain bothalkyl substituents (short chain branches) as well as long chainbranches. Most LDPE polymers are homopolymers, although some arecopolymers and interpolymers, typically using other α-olefin comonomers.

Chain transfer agents (CTAs), or “telogens”, are often used to controlthe melt index in a free-radical polymerization process. “Chaintransfer” involves the termination of growing polymer chains, thuslimiting the ultimate molecular weight of the polymer material. Chaintransfer agents are typically hydrogen atom donors that react with agrowing polymer chain and stop the polymerization reaction of the chain.Known CTAs include many types of hydrogen atom donor compounds, such assaturated or unsaturated hydrocarbons, aldehydes, ketones, and alcohols.By manipulating the concentration and type of chain transfer agent usedin a process, one can affect the average length and molecular weightdistribution of the polymer chains. This in turn affects the melt index(I₂ or MI), which is related to molecular weight.

Many chain transfer agents are known in the art for use inhigh-pressure, low density polyethylene production. References thatdisclose the use of chain transfer agents in free-radical polymerizationof ethylene and ethylene-based polymers include Ehrlich, P., andMortimer, G. A., “Fundamentals of the Free-Radical Polymerization ofEthylene”, Advanced Polymers, Vol. 7, 386-448 (1970); Mortimer, GeorgeA., “Chain Transfer in Ethylene Polymerization—IV. Additional Study at1360 Atm and 130° C.”, Journal of Polymer Science, Part A-1, Vol. 8,1513-23 (1970); Mortimer, George A., “Chain Transfer in EthylenePolymerization—VI. The Effect of Pressure”, Journal of Polymer Science,Part A-1, Vol. 8, 1543-48 (1970); Mortimer, George A., “Chain Transferin Ethylene Polymerization—VII. Very Reactive and Depletable TransferAgents”, Journal of Polymer Science, Part A-1, Vol. 10, 163-168 (1972);Great Britain Patent No. 997,408 (Cave); U.S. Pat. No. 3,377,330(Mortimer); U.S. Patent Publication No. 2004/0054097 (Maehling, et al.);and U.S. Pat. Nos. 6,596,241; 6,673,878; and 6,899,852 (Donck).

After hydrogen atom donation, it is known that a chain transfer agentmay form a radical which can start a new polymer chain. The result isthat the original CTA is incorporated into a new or existing polymerchain, thereby introducing a new functionality into the polymer chainassociated with the original CTA. The CTA may introduce newfunctionality into the polymer chain that is not normally the result ofthe monomer/comonomer polymerization.

Low density ethylene-based polymers produced in the presence of CTAs aremodified in a number of physical properties, such as processability;film optical properties such as haze, gloss and clarity; density;stiffness; yield point; film draw; and tear strength. For example, anα-olefin acting as a CTA could also introduce a short chain branch intoa polymer chain upon incorporation.

SUMMARY OF THE INVENTION

Disclosed is an ethylene-based polymer with a density from about 0.90 toabout 0.94 in grams per cubic centimeter, with a molecular weightdistribution (M_(w)/M_(n)) from about 2 to about 30, a melt index (I₂)from about 0.1 to about 50 grams per 10 minutes, and further comprisingsulfur from about 5 to about 4000 parts per million. The amount ofsulfur in the ethylene-based polymer is determined using a procedurecalled the Total Sulfur Concentration method, described infra. Theamount of sulfur is also determined based upon the total weight of theethylene-based polymer. In some disclosed ethylene-based polymers, thepolymer is a homopolymer.

Also disclosed is an ethylene-based polymer with long chain branching.The long chain branching is characterized by a gpcBR value greater than0.05 as determined by the gpcBR Branching Index, described infra. Thelong chain branching is also characterized by a GPC-LS Characterizationvalue greater than 2.1 as determined by the GPC-LS Characterizationmethod, described infra. In some disclosed ethylene-based polymers, theGPC-LS Characterization value is from about 2.1 to about 10.

Also disclosed is an ethylene-based polymer with a zero-shear viscosity,η₀, in Pascal-seconds at 190° C. as determined using a Zero ShearViscosity method, described infra, an absolute weight average molecularweight value, M_(w, Abs), in grams per mole, and a conventional weightaverage molecular weight value, M_(w, GPC). These properties for some ofthe disclosed ethylene-based polymer have the following numericalrelationship:(3.6607*Log M _(w,Abs))−16.47<Log η₀*(M _(w,GPC) M _(w,Abs))<(3.6607*LogM _(w,Abs))−14.62,

Also disclosed is an ethylene-based polymer with a surface haze, S, aninternal haze, I, both in units of % haze and both determined using aSurface and Internal Haze method, described infra, and a melt index (I₂)in grams per 10 minutes. These properties for the disclosedethylene-based polymer have the following numerical relationship:S/I≦(−0.057*I ₂)+1.98,preferably wherein the ethylene-based polymer comprises sulfur.

Disclosed is a process for making an ethylene-based polymer adduct whichincludes the steps of splitting a process fluid, a portion of whichcomprises ethylene, for delivery into a tubular reactor, into anupstream process feed stream and at least one downstream process feedstream; feeding the upstream process feed stream into a first reactionzone and the at least one downstream process feed stream into an atleast one other reaction zone to recombine the process fluid, whereinside the tubular reactor in at least one of several reaction zones theprocess fluid has an average velocity of at least 10 meters per second;and initiating a free-radical polymerization reaction inside the tubularreactor so as to produce an ethylene-based polymer adduct and heat. Thedisclosed process includes a tubular reactor comprised of severalreaction zones including a first reaction zone and at least one otherreaction zone. The disclosed process also includes an upstream processfeed stream that is further comprised of at least one chain transferagent with a chain transfer constant, Cs, greater than 1. In somedisclosed processes, the at least one chain transfer agent with a Csgreater than 1 has a concentration in the upstream process feed streamthat is higher than any concentration of the at least one chain transferagent with a Cs greater than 1 in any of the at least one downstreamprocess feed streams. In some disclosed processes, the process fluidfurther comprises at least one chain transfer agent with a Cs less than1.

Disclosed is another process for making an ethylene-based polymer adductwhich includes the steps of feeding a process fluid via an upstreamprocess feed stream into a first reaction zone of a tubular reactor,where the process fluid has an average velocity in the tubular reactorin at least one of several reaction zones of at least 10 meters persecond; and initiating a free-radical polymerization reaction inside thetubular reactor so as to produce an ethylene-based polymer adduct andheat. The disclosed process includes a tubular reactor comprised ofseveral reaction zones including a first reaction zone and at least oneother reaction zone. The disclosed process also includes an upstreamprocess feed stream that is further comprised of at least one chaintransfer agent with a chain transfer constant, Cs, greater than 1. Insome disclosed processes, the process fluid further comprises at leastone chain transfer agent with a Cs less than 1.

BRIEF DESCRIPTION OF THE DRAWINGS

The Summary as well as the Detailed Description will be betterunderstood when read in conjunction with the appended drawings. Itshould be understood, however, that the scope of the claimed inventionsare not limited to the precise arrangements and instrumentalities shown.The components in the drawings are not necessarily to scale. In thedrawings, like reference numerals designate corresponding partsthroughout the several views.

FIG. 1 is a diagram of a process describing the elements of a disclosedtube reactor system 100;

FIG. 2 is a concentration-normalized light scattering (LS) chromatographcurve for a range of log conventionally calibrated GPC molecular weightand parts of the GPC-LS Characterization analysis for Example 1;

FIG. 3 is a concentration-normalized light scattering (LS) chromatographcurve for a range of log conventionally calibrated GPC molecular weightand parts of the GPC-LS Characterization analysis for ComparativeExample 4;

FIG. 4 is a diagram of the process reaction system 200 that is used tomanufacture Examples 1 and 2 as well as Comparative Examples 1-3;

FIG. 5 is a plot of Zg, or Log η₀*(M_(w, GPC)/M_(w, Abs)), versus thelogarithm of absolute molecular weight, M_(w, Abs), for Examples 1 and2, Comparative Examples 1-46, and Linear Standard 1;

FIG. 6 is a plot of the surface/internal haze ratio versus melt index(I₂) for Examples 1 and 2 as well as for Comparative Examples 1-4 and47-82;

FIG. 7 is a chart of melt index (I₂) versus extrusion pass number versusfor Example 1 and Comparative Example 3 under atmospheric conditions;

FIG. 8 is a plot of viscosity versus frequency as determined by DynamicMechanical Spectroscopy for Examples 1 and 2 and Comparative Examples1-4;

FIG. 9 is a plot of tan delta versus frequency as determined by DynamicMechanical Spectroscopy for Examples 1 and 2 and Comparative Examples1-4;

FIG. 10 is a plot of phase angle versus G* as determined by DynamicMechanical Spectroscopy for Examples 1 and 2 and Comparative Examples1-4.

DESCRIPTION OF EMBODIMENTS OF THE INVENTION

The inventive compositions are low density ethylene-based polymershaving a narrow molecular weight distribution, which can be used forblown and cast films used alone or in blends with other polymers,created in a free-radical polymerization of ethylene, and optionally acomonomer, in the presence of at least one chain transfer agent (CTA).At least one of the chain transfer agents is a high-activity CTA, suchas tert-dodecyl mercaptan (TDM).

In typical high pressure free radical LDPE production processes,“low-activity” chain transfer agents are typically used to controlreactions in the process. A low-activity CTA has a chain transferconstant (Cs) that is less than 1. For example, at certain conditionspropionaldehyde has a Cs˜0.33 as reported in Mortimer, George A., “ChainTransfer in Ethylene Polymerization—VII. Very Reactive and DepletableTransfer Agents”, Journal of Polymer Science, Part A-1, Vol. 10, 163-168(1972). The chain transfer constant, Cs, for a chain transfer agent isdefined as the ratio of the reaction rate constant for the chaintransfer agent relative to the reaction rate constant for propagation ofthe monomer.

A “high-activity” chain transfer agent (Cs greater than or equal to 1)is a chain transfer agent that has a sufficiently high degree ofactivity during free-radical polymerization that the growing monomerchain will more likely accept the hydrogen atom donation given theopportunity rather than propagate with another monomer molecule. In suchcases where the Cs is greater than one, the high-activity CTA in theprocess fluid is consumed in a manner where the relative concentrationof the chain transfer agent diminishes with respect to the concentrationof monomer as the reaction proceeds forward in time. If the reactioncontinues and no additional chain transfer agent is provided, thehigh-activity CTA will become depleted. It is feasible that a reactionsystem may not have enough, if any, chain transfer agent to controlmolecular weight.

By using a high-activity chain transfer agent at the beginning of theprocess with a Cs range of greater than 1 and can be up to 5,000,preferably up to 500, the formation of the high-molecular weight polymerchains is suppressed at the beginning of the process. This results inpolymers with a narrower molecular weight distribution. The suppressionprevents the formation of highly branched, high-molecular weight polymerchains that form in the later stages of the process.

There are other benefits of using a high-activity CTA to suppresshigh-molecular weight polymer chain formation in the early part of theprocess. The suppression improves the overall single-pass processconversion by improving process system performance.

However, effectively using a high-Cs chain transfer agent by itself in afree-radical polymerization process is challenging. One means of doingso would be by adding additional high-Cs CTAs later in the process.Another means would be to incorporate at the beginning of the process acombination of at least one high-Cs CTA and at least one low-Cs CTA. Insuch a process in which as the reaction proceeds from beginning to end,the high-activity CTA is preferentially consumed during the period whenthe monomer is in relatively high concentration, especially in tubularreactor systems with more than one reaction zone (i.e., initiatorinjection points. Later in the process, when both monomer and high-CsCTA have been relatively depleted, the low-Cs CTA, which has notsignificantly reacted with the forming polymer chains because of itsrelative reaction rates and concentrations as compared to the monomer,has a greater influence over the process by supporting chain transfer tocontrol molecular weight.

Additionally, polymers produced in the presence of chain transferagents, especially high-Cs chain transfer agents, may have interestingphysical and chemical properties due to incorporation of the chaintransfer agents. Properties that may be modified include itsprocessibility (e.g., shear viscosity), optical properties such as hazeand clarity, density, stiffness, yield point, film draw and tearstrength.

A low density ethylene-based polymer is disclosed that has a densityfrom about 0.90 to about 0.94 g/cm³, a molecular weight distribution,M_(w)/M_(n), from about 2 to about 30, and a melt index, I₂, from about0.1 to about 50 grams per 10 minutes. The amount of sulfur in theethylene-based polymer is based upon the total weight of theethylene-based polymer and is determined using the Total SulfurConcentration method.

The low density ethylene-based polymer may be a homopolymer of ethyleneor it may be an ethylene-based interpolymer comprised of ethylene and atleast one comonomer. Comonomers useful for incorporation into anethylene-based interpolymer, especially an ethylene/α-olefininterpolymer include, but are not limited to, propylene, isobutylene,1-butene, 1-pentene, 1-hexene, 3-methyl-1-pentene, 4-methyl-1-pentene,and 1-octene, non-conjugated dienes, polyenes, butadienes, isoprenes,pentadienes, hexadienes (for example, 1,4-hexadiene), octadienes,styrene, halo-substituted styrene, alkyl-substituted styrene,tetrafluoroethylenes, vinylbenzocyclobutene, naphthenics, cycloalkenes(for example, cyclopentene, cyclohexene, cyclooctene), and mixturesthereof. Ethylene is frequently copolymerized with at least one C₃-C₂₀α-olefin, such as propene, 1-butene, 1-hexene and 1-octene.

The low density ethylene-based polymer may further comprise sulfur,where the sulfur may be at least 5 ppm total sulfur concentration basedupon the total weight of the ethylene-based polymer. The sulfur that isincorporated into the ethylene-based polymer originates from the use ofa high Cs chain transfer agent with sulfur as part of its molecularstructure. Some mercaptans, such as tert-dodecyl mercaptan, are high-Cschain transfer agents and preferentially incorporate into ethylene-basedpolymer chains during free-radical polymerization to effect chaintransfer. It is believed that incorporation of sulfur intoethylene-based polymers will lead to improved properties such asoxidative resistance.

Additionally, “free sulfur” compounds, or sulfur-containing compoundsincluded as a byproduct and other compounds homogeneously incorporatedwith the ethylene-based polymer, are also present.

The low density ethylene-based polymer can exhibit a numericalrelationship between internal haze, surface haze, and I₂ melt index ofthe polymer that is different than other low density ethylene-basedpolymers. Further disclosed is an ethylene-based polymer with asurface/internal haze ratio versus melt index (I₂) relationship for arange of I₂ of about 0.1 to about 1.5 grams per 10 minutes. Furtherdisclosed is an ethylene-based polymer with a surface/internal hazeratio versus melt index relationship that is further comprised ofsulfur. Further disclosed is an ethylene-based polymer with asurface/internal haze ratio versus melt index relationship that exhibitslong chain branching as characterized by a gpcBR value greater than 0.05as determined by a gpcBR Branching Index by 3D-GPC method.

Disclosed is a low density ethylene-based polymer further comprisingsulfur that exhibits a numerical relationship between conventionallycalibrated molecular weight, M_(w, GPC), and an absolute molecularweight, M_(w, Abs), both in grams per mole as determined by the TripleDetector Gel Permeation Chromatography method, described infra, and azero shear viscosity, η₀, in Pascal-seconds at 190° C., as determined bythe Zero Shear Viscosity method, described infra. Further disclosed isan ethylene-based polymer with a conventionally calibrated molecularweight, an absolute molecular weight, and a zero shear viscosityrelationship that exhibits long chain branching as characterized by agpcBR value greater than 0.05 as determined by a gpcBR Branching Indexby the 3D-GPC method.

Disclosed is a low density ethylene-based polymer that exhibits arelationship between the concentration-normalized light scattering (LS)response value and the logarithm value of conventionally calibratedmolecular weight, M_(w, GPC), that is different than that of other lowdensity ethylene-based polymers. The difference is captured in arelationship called a GPC-LS Characterization value (Y). The GPC-LSCharacterization value (Y) is determined by the GPC-LS Characterizationmethod, described infra. Disclosed is an ethylene-based polymer having aGPC-LS Characterization value (Y) of greater than 2.1 and has long chainbranching. Long chain branching is characterized by a gpcBR valuegreater than 0.05 as determined by a Determination of gpcBR BranchingIndex by the 3D-GPC method. Also disclosed is an ethylene-based polymerhaving a GPC-LS Characterization value (Y) of greater than 2.3,preferably greater than 2.4. Also disclosed is an ethylene-based polymerwith the given GPC-LS Characterization values (Y) in a range of about2.1 to about 10. Also disclosed is an ethylene-based polymer with thegiven GPC-LS Characterization values (Y) that is further comprised ofsulfur.

The disclosed processes are high pressure free radical reactor processesfor the polymerization of ethylene and, optionally, at least onecomonomer, to produce a low density ethylene-based polymer adduct andbyproduct heat. The disclosed processes use at least one high-Cs (and insome cases a mixture of at least one high-Cs and at least one low-Cs)chain transfer agent(s) to assist in the formation of a narrowermolecular weight distribution low density ethylene-based polymer thantraditionally made.

One process of the invention involves a free-radical initiated lowdensity ethylene-based polymerization reaction in a tubular reactorprocess. Besides feeding the reactor ethylene and, optionally, at leastone comonomer, other components are fed to the reactor to initiate andsupport the free radical reaction as the ethylene-based polymer adductis formed, such as reaction initiators, catalysts, and chain transferagents. The process is a tubular polymerization reaction where a processfluid partially comprised of ethylene is free-radically polymerizedcreating a highly exothermic reaction. The reaction occurs under highoperating pressure (1000 bar to 4000 bar) in turbulent process fluidflow (hence low density ethylene-based polymers also referred to as“high pressure” polymers) at maximum temperatures in the reactor of 160°C. to 360° C., while the initial initiation temperature for the reactionis between 120° C. to 200° C. At certain points along the tube, aportion of the heat produced during the free-radical polymerization maybe removed through the tube wall. Typical single-pass conversion valuesfor a tubular reactor range from about 20 to 40 percent. Tubular reactorsystems typically also include at least one monomer recycle loop toimprove conversion efficiency.

A typical tubular polymerization reaction system is shown in FIG. 1. Atube reactor system 100 has a tube 2 with a length typically from about250 to about 2000 meters. The length and diameter of the tube affectsthe residence time and velocity of the process fluid as well as the heataddition/removal capacity of tube 2. Suitable, but not limiting, reactorlengths can be between 100 and 3000 meters, and some between 500 and2000 meters. Tube 2 also has a working internal diameter from about 30to about 100 mm based upon desired system throughput, operationalpressure range, and the degree of turbulent flow for mixing andreaction. The working internal diameter may widen and narrow at pointsalong tube 2 to accommodate different portions of the process, such asturbulent mixing, injection of reaction initiators and feeds, andprocess fluid throttling (i.e., accelerating process fluid velocity atthe expense of pressure loss).

For processes of this invention, the average velocity of the processfluid is at least 10 meters per second, and even as high as 25 metersper second. Process fluid velocity is important for a numbers ofreasons, including overall process throughput, ethylene conversion, heatremoval capacity, and, for processes with a number of reaction zones,management of local reaction initiation temperatures and injectionamounts of chain transfer agents and process initiators.

Referring to FIG. 1 and tube reactor system 100, a primary compressor 4,which may be a multi-stage compressor or two or more compressors runningin parallel, is connected at its intake side to a source of freshmonomer/comonomer feed called fresh feed conduit 6 and a low pressuresystem recycle conduit 8.

Still referring to FIG. 1, a second compressor, in some cases called ahypercompressor 5, which may be a multi-stage compressor, is connectedat its intake to the discharge of the primary compressor 4 as well asthe second of the two recycle streams called the high pressure systemrecycle conduit 26.

After pressurization by the hypercompressor 5, the process fluid is fedinto the tube 2 through conduit 12 as an upstream process feed stream.In some disclosed processes, the process fluid is split and fed to tube2 at different feed locations. In such processes, part of the processfluid is fed to tube 2 through conduit 12 as an upstream process feedstream to the first reaction zone and the other parts (depending on thenumber of splits made in the process fluid) would be fed to tube 2 asdownstream process feed streams to the other reaction zones throughvarious conduits 14.

As disclosed, a process using several reaction zones with fresh feeds,including a first reaction zone and at least one other reaction zone,improves overall ethylene conversion by removing heat in the systemthrough the introduction of feed streams (i.e., initiator, monomer)downstream of the first reaction zone that are cooler than the processfluid in the tube 2. Tubular reactor systems with multiple reaction andfeed zones permit the tube reactor to operate at an overall loweraverage peak reactor temperature. This assumes that conversion betweenthe multiple reactor or feed zones and analogous non-multiple reactionor feed zone tubular reactors are kept the same. See Goto, et al., J.Appl. Polymer Science, Appl. Polymer Symp., Vol. 36, 21 (1981). Onereason for this is that the downstream process feed passing throughconduits 14 may be cooled before injection into the reaction system oris inherently colder, thereby reducing the overall reaction processfluid temperature before (re)initiation of polymerization. As previouslymentioned, cooling of the process would permit additional initiator tobe added, thereby improving single-pass conversion ofmonomer/comonomers. In such disclosed processes, the temperature of thedownstream process feed stream(s) are preferably below 120° C., morepreferably below 50° C., and most preferably below 30° C. Lower averagereactor temperatures are important because it reduces the overall levelof long chain branching, which produces narrower MWD products.Additionally, the use of multiple feed locations along the tube are alsopreferable for producing narrow MWD resins for use in applications suchas film resins where optical properties are important. Multiple feedlocations may also result in a narrowing of the molecular weightdistribution relative to analogous systems that do not have multiplereaction zones.

In disclosed processes where there are more than one reaction zone, oneor more free-radical initiator or catalyst conduits 7 convey initiatoror catalyst to tube 2 near or at the beginning of each reaction zone.

The type of free radical initiator to be used is not critical. Examplesof free radical initiators include oxygen-based initiators such asorganic peroxides (PO). Preferred initiators are t-butyl peroxypivalate, di-t-butyl peroxide, t-butyl peroxy acetate, and t-butylperoxy-2-ethylhexanoate, and mixtures thereof. These organic peroxyinitiators are used in conventional amounts of between 0.0001 and 0.01weight percent based upon the weight of high pressure feed.

The free-radical polymerization reaction resulting in the disclosedethylene-based polymer adduct occurs in each reaction zone whereinitiator or catalyst is present. The reaction is an exothermic reactionthat generates a large quantity of heat. Without cooling, the adiabatictemperature rise in the process fluid and the ethylene-based polymeradduct (which absorbs and retains heat) would result in unfavorablereactions. Such reactions may include ethylene decomposition (whereethylene and polyethylene break down in a combustionless reaction intobase products) or excessive long chain branching, which would lead to abroadening of the molecular weight distribution.

In typical processes, high molecular weight polymer chains form and“plate out” on the insides of reactor tube walls, insulating the processand hindering heat removal. In the disclosed processes, which includeuse of a high-Cs chain transfer agent and a process fluid velocity above10 meters per second, the extent to which this insulative layer forms isreduced. This improves the heat removal process versus a comparableprocess that does not use a high-Cs chain transfer agent. Also, in someembodiments the process fluid in tube 2 is periodically cooled directlyby the addition of downstream process feed stream(s) from conduit 14.Because heat removal is improved versus a comparable process that doesnot use a high-Cs chain transfer agent or cooled downstream process feedstreams, the process fluid in tube 2 enters the at least one otherreaction zones at a lower reinitiation temperature; therefore leading toimproved single pass process conversion. This permits the addition of agreater amount of catalyst or initiator to reach a similar peak processfluid temperature during each reaction reinitiation, if needed.

When delivering a high-Cs chain transfer agent to the process, theimpact on the ability to remove heat from the tubular reactor duringsteady-state operations can be seen as compared to when a high-Cs CTA isnot used. In some disclosed processes, as compared to similar andanalogous processes where conditions are otherwise equivalent and are atsteady-state but do not use a high-Cs CTA:

(a) at least 1% and preferably at least 3% more heat is removed from atleast one reaction zone; and/or

(b) the average temperature difference between the inlet and the outlettemperatures (the temperature “delta”) of a heat removal medium used ina heat exchanger that removes heat from a reaction system isstatistically significantly higher (i.e., greater than 3 times thestandard deviation of the temperature delta over a fixed period of time)than that of an analogous heat removal medium used in an analogous heatexchanger in an analogous process; and/or

(c) the difference in the outlet temperature of the heat removal mediumused in a heat exchanger that removes heat from a reaction system is atleast 1° C. higher for a fixed period of time than that of an analogousheat removal medium used in an analogous heat exchanger in an analogousprocess.

In disclosed processes, at least one chain transfer agent is added tothe process fluid which has a Cs greater than one. In some disclosedprocesses, at least two chain transfer agents—one with a Cs greater thanone and another with a Cs less than one—are added to the process fluid.More than one chain transfer agent may be used to take advantage ofrelative properties during free-radical polymerization inside tube 2.

In disclosed processes, chain transfer agents are added so as to blendas homogeneously as possible with the process fluid before introductionto the tube 2. Depending on the physical layout of the tube reactorsystem 100 and chemical characteristics of the process fluid and theCTAs, such blending may be achieved by injecting the CTAs at the inletof the booster compressor 21 for the low pressure system recycle conduit8, in the inlet of the primary compressor 4, in the inlet of thehypercompressor 5, at the outlet of the hypercompressor 5, at the inletof the tube 2 or together with the first peroxide injection.

Although not shown in FIG. 1, selective feeding of CTAs to the tubereactor 2 is possible. In such cases, the CTAs may be fed into the tube2 selectively by being injected into conduits 12 or 14 instead of usingthe CTA source 23 as shown in FIG. 1. In specific cases, the CTAs may beinjected from CTA source 23 only into the upstream process feed streamvia conduit 12. This flexibility in the disclosed process regarding theinjection of CTAs from CTA source 23 permits selective injection of CTAsonly into the first reaction zone, or only into a different reactionzone, or into some or all of the reaction zones. It also permits theinjection of different CTAs, including CTAs with different Cscharacteristics, to be injected from CTA source 23 into different zones(e.g., a high-Cs CTA injected into the first reaction zone and a low-CsCTA injected into the at least one other reaction zones) to optimizereaction system performance and ethylene-based polymer adductproperties.

In some disclosed processes where more than one CTA is used, one of thechain transfer agents has a Cs less than one and another chain transferagent has a Cs greater than one. In such processes, the chain transferagents may be fed to the system at different feed rates or amounts so asto customize their effectiveness in different parts of the process or tooptimize the ethylene-based polymer properties. In some other disclosedprocesses, the feed rate of the low activity CTA may be regulated by theamount of recycled low activity CTA detected in either or both recyclestreams 26 and 8. The feed amounts, ratio of chain transfer agents toeach other, and relative amount of chain transfer agent to the amount ofethylene in the fresh feed conduit 6 will vary depending on severalfactors, including but not limited to the tube 2 and tube reactor system100 geometry, production rates, the relative activities of the chaintransfer agents, and the overall tube 2 residence time. The feed amountsand ratio of chain transfer agents may also be regulated based uponfinal ethylene-based polymer characteristics, such as melt viscosity,overall production amount, target molecular weight distribution, desiredmelt index, first zone peak temperature, residual CTAs or CTAbyproducts, and tube process fluid velocity.

In disclosed processes, the concentration of chain transfer agent in theprocess fluid is from about 1 to about 600 molar ppm, and preferablyfrom about 1 to about 200 molar ppm. In some disclosed processes, theconcentration of the high-Cs CTA in the upstream process feed stream isfrom about 1 to about 600 molar ppm, and preferably from about 1 toabout 200 molar ppm. In such disclosed processes, the disclosed CTAconcentrations are found in the upstream process feed stream, such asconduit 12. In other disclosed processes, the CTA molar flow ratio,which is the ratio of the high-Cs CTA in moles/hour to the low-Cs CTA inmoles/hour in the process fluid, is from about 0.01 to about 100,preferably from about 0.05 to about 5, and more preferably from about0.05 to about 0.5.

Referring to FIG. 1, a mixture of ethylene-based polymer formed from thereaction, unreacted monomer (and comonomer), and unused feeds, such assolvents and CTAs, or degradation and side reaction products, passesfrom the tube outlet 16 to the separations part of the process. Theseparating and recycling part of the tube reactor system 100 processincludes a high-pressure separator (HPS) 18, which receives the productpolymer and process fluid mixture from the outlet of the tube 2. Thetails of the HPS 18 conveys the polymer adduct and any remainingunreacted monomer/comonomer and other unused feeds that might bedissolved with the polymer adduct, to the low-pressure separator (LPS)20. The higher pressure lights stream passes through the high pressuresystem recycle conduit 26, which may include a refining system 24 tocool and purify the stream and purge inert gases, and rejoins theprocess fluid passing from the primary compressor 4 to thehypercompressor 5.

When the heat removal medium is a liquid, a heat exchanger 30, may beused to effect heat transfer and cool the process fluid and theethylene-based polymer adduct.

In the disclosed processes, there is an overall improvement in ethyleneconversion. The overall improvement comes from the reduction information of high-molecular weight polymers chains early in the process,improvements in heat transfer, and from the ability to use morefree-radical initiator. Given comparable steady state conditions, theimprovement in the ethylene conversion for a disclosed process using atleast one chain transfer agent with a Cs greater than 1 is at least 0.3percent higher than the ethylene conversion in an analogous processlacking a chain transfer agent with a Cs greater than 1.

End-Uses

End-use products made using the disclosed ethylene-based polymersinclude all types of films (for example, blown, cast and extrusioncoatings (monolayer or multilayer)), molded articles (for example, blowmolded and rotomolded articles), wire and cable coatings andformulations, cross-linking applications, foams (for example, blown withopen or closed cells), and other thermoplastic applications. Thedisclosed ethylene-based polymers are also useful as a blend componentwith other polyolefins.

The types of films that make be produced as end-use products from thedisclosed ethylene-based polymers include silage films, sealants,silobags, stretch films, display packaging, shrink films, and heavy dutyshipping sacks. Additionally, blown, cast and extrusion coatings(monolayer or multilayer) also may be produced using the disclosedethylene-based polymers.

Definitions

The terms “blend” or “polymer blend” means a mixture of two or morepolymers. A blend may or may not be miscible (not phase separated atmolecular level). A blend may or may not be phase separated. A blend mayor may not contain one or more domain configurations, as determined fromtransmission electron spectroscopy, light scattering, x-ray scattering,and other methods known in the art.

The term “comparable” means similar or like. For a given process,comparable means that for two or more process runs using the samephysical process equipment (hence the process units in each run areanalogous to one another), the difference between the peak temperaturevalues for each analogous reaction zone (e.g., Reaction Zone 1—PeakTemperature of Example 1 and Reaction Zone 1—Peak Temperature ofComparative Example 1) for each of the several reaction zones is within1° C. for the process to be deemed comparable.

The basis of comparison is for a period of 2.5 hours of steady-stateconditions using 10 minute average data (as opposed to “spot data”,which are individual data readings at specific points in time).

The term “composition” includes a mixture of materials which comprisethe composition as well as reaction products and decomposition productsformed from interaction and reaction between the materials of thecomposition.

The term “ethylene-based polymer” refers to a polymer that is formedfrom more than 50 mole percent polymerized ethylene monomer (based onthe total amount of polymerizable monomers), and, optionally, one ormore comonomers. A homopolymer of ethylene is an ethylene-based polymer.

The term “ethylene/α-olefin interpolymer” refers to an interpolymer thatis formed from more than 50 mole percent polymerized ethylene monomer(based on the total amount of polymerizable monomers), and at least oneα-olefin comonomer.

The term “homopolymer” is a polymer that is formed from only a singletype of monomer, such as ethylene.

The term “interpolymer” refers to polymers prepared by thecopolymerization of at least two different types of monomers. The terminterpolymer includes copolymers, usually employed to refer to polymersprepared from two different monomers, and polymers prepared from morethan two different types of monomers, such as terpolymers.

The term “LDPE” may also be referred to as “high pressure ethylenepolymer” or “highly branched polyethylene” and is defined to mean thatthe polymer is partly or entirely polymerized in autoclave or tubularreactors at pressures above 13,000 psig with the use of free-radicalinitiators, such as peroxides (see, for example, U.S. Pat. No. 4,599,392(McKinney, et al.)).

The term “polymer” refers to a compound prepared by polymerizing one ormore monomers, whether of the same or a different type of monomer. Theterm polymer embraces the terms “homopolymer” and “interpolymer”.

The term “sulfur containing compound” is a compound containing a —S—functional group in addition to carbon atoms substituted with hydrogenatoms, where a portion of the hydrogen atoms can be substituted by inertsubstituents or moieties. The presence of units derived from a sulfurgroup containing compound, such as mercaptans, can quantitatively bedetermined using known techniques, for example, by the Total SulfurConcentration method given infra.

Testing Methods

Density: Samples for density measurement of a polymer are preparedaccording to ASTM D 1928. Measurements are made within one hour ofsample pressing using ASTM D792, Method B.

Melt Index: Melt index, or I₂, of an ethylene-based polymer is measuredin accordance with ASTM D 1238, Condition 190° C./2.16 kg.

Melt Strength: Melt strength measurements are conducted on a GottfertRheotens 71.97 (Göettfert Inc.; Rock Hill, S.C.) attached to a GottfertRheotester 2000 capillary rheometer. A polymer melt is extruded througha capillary die with a flat entrance angle (180 degrees) with acapillary diameter of 2.0 mm and an aspect ratio (capillarylength/capillary radius) of 15. After equilibrating the samples at 190°C. for 10 minutes, the piston is run at a constant piston speed of 0.265mm/second. The standard test temperature is 190° C. The sample is drawnuniaxially to a set of accelerating nips located 100 mm below the diewith an acceleration of 2.4 mm/second². The tensile force is recorded asa function of the take-up speed of the nip rolls. Melt strength isreported as the plateau force (cN) before the strand broke. Thefollowing conditions are used in the melt strength measurements: Plungerspeed=0.265 mm/second; wheel acceleration=2.4 mm/s²; capillarydiameter=2.0 mm; capillary length=30 mm; and barrel diameter=12 mm.

Dynamic Mechanical Spectroscopy: Dynamic Mechanical Spectroscopy (DMS)Dynamic oscillatory shear measurements are performed with the ARESsystem of TA Instruments (New Castle, Del.) at 190° C. using 25 mmparallel plates at a gap of 2.0 mm and at a constant strain of 10% underan inert nitrogen atmosphere. The frequency interval is from 0.03 to 300radians/second at 5 points per decade logarithmically spaced. The stressresponse was analyzed in terms of amplitude and phase, from which thestorage modulus (G′), loss modulus (G″), complex modulus (G*), tan δ,phase angle δ and complex viscosity (η*) were calculated. The complexmodulus, G*, is a complex number with G′ as its real and G″ as itsimaginary components, respectively (G*=G′±iG″). The magnitude of G* isreported as |G*|=(G′²+G″²)^(1/2). Both tan δ and the phase angle δ arerelated to the material's relative elasticity. Tan δ is the ratio of theloss modulus to the storage modulus

$\left( {{\tan\;\delta} = \frac{G^{''}}{G^{\prime}}} \right)$and the phase angle δ can be obtained from

$\delta = {\tan^{- 1}{\frac{G^{''}}{G^{\prime}}.}}$The complex viscosity η* is also a complex number with η′ as its realand η″ as its imaginary components, respectively. The magnitude of η* isreported as

${\eta^{*} = {\left( {\eta^{\prime 2} + \eta^{\prime 2}} \right)^{1/2} = \left\lbrack {\left( \frac{G^{''}}{\omega} \right)^{2} + \left( \frac{G^{\prime}}{\omega} \right)^{2}} \right\rbrack^{1/2}}},$where ω is the angular frequency in radians/second.

DSC: Differential Scanning calorimetry (DSC) can be used to measure thecrystallinity of a sample at a given temperature for a wide range oftemperatures. For example, a TA Instruments Q1000 DSC, equipped with aRCS (Refrigerated Cooling System) and an autosampler module is used toperform this analysis. During testing, a nitrogen purge gas flow of 50ml/min is used. Each sample is pressed into a thin film and melted inthe press at about 175° C.; the melted sample is then air-cooled to roomtemperature (˜25° C.). A 3-10 mg, 6 mm diameter specimen is extractedfrom the cooled polymer, weighed, placed in a light aluminum pan (ca 50mg), and crimped shut. Analysis is then performed to determine itsthermal properties. The thermal behavior of the sample is determined byramping the sample temperature up and down to create a heat flow versustemperature profile. First, the sample is rapidly heated to 180° C. andheld isothermal for 3 minutes in order to remove its thermal history.Next, the sample is cooled to −40° C. at a 10° C./minute cooling rateand held isothermal at −40° C. for 3 minutes. The sample is then heatedto 150° C. (this is the “second heat” ramp) at a 10° C./minute heatingrate. The cooling and second heating curves are recorded. The cool curveis analyzed by setting baseline endpoints from the beginning ofcrystallization to −20° C. The heat curve is analyzed by settingbaseline endpoints from −20° C. to the end of melt. The valuesdetermined are peak melting temperature (T_(m)), peak crystallizationtemperature (T_(c)), the heat of fusion (H_(f)) (in Joules per gram),and the % crystallinity for polyethylene samples calculated usingEquation 1:% Crystallinity=[(H _(f)(J/g))/(292J/g)]×100  (Eq. 1)The heat of fusion (H_(f)) and the peak melting temperature are reportedfrom the second heat curve. The peak crystallization temperature isdetermined from the cooling curve.

Triple Detector Gel Permeation Chromatography: The Triple Detector GelPermeation Chromatography (3D-GPC or TD-GPC) system consists of a Waters(Milford, Mass.) 150 C high temperature chromatograph (other suitablehigh temperatures GPC instruments include Polymer Laboratories(Shropshire, UK) Model 210 and Model 220 equipped with an on-boarddifferential refractometer (R1). Additional detectors can include an IR4infra-red detector from Polymer ChAR (Valencia, Spain), PrecisionDetectors (Amherst, Mass.) 2-angle laser light scattering (LS) detectorModel 2040, and a Viscotek (Houston, Tex.) 150R 4-capillary solutionviscometer. A GPC with these latter two independent detectors and atleast one of the former detectors is sometimes referred to as “3D-GPC orTD-GPC” while the term “GPC” alone generally refers to conventional GPC.Depending on the sample, either the 15° angle or the 90° angle of thelight scattering detector is used for calculation purposes. Datacollection is performed using Viscotek TriSEC software, Version 3, and a4-channel Viscotek Data Manager DM400. The system is also equipped withan on-line solvent degassing device from Polymer Laboratories(Shropshire, United Kingdom).

Suitable high temperature GPC columns can be used such as four 30 cmlong Shodex HT803 13 micron columns or four 30 cm Polymer Labs columnsof 20-micron mixed-pore-size packing (MixA LS, Polymer Labs). The samplecarousel compartment is operated at 140° C. and the column compartmentis operated at 150° C. The samples are prepared at a concentration of0.1 grams of polymer in 50 milliliters of solvent. The chromatographicsolvent and the sample preparation solvent contain 200 ppm of butylatedhydroxytoluene (BHT) in trichloro benzene (TCB). Both solvents aresparged with nitrogen. The polyethylene samples are gently stirred at160° C. for four hours. The injection volume is 200 microliters. Theflow rate through the GPC is set at 1 ml/minute.

The GPC column set is calibrated by running 21 narrow molecular weightdistribution polystyrene standards. The molecular weight (MW) of thestandards ranges from 580 to 8,400,000, and the standards are containedin 6 “cocktail” mixtures. Each standard mixture has at least a decade ofseparation between individual molecular weights. The standard mixturesare purchased from Polymer Laboratories. The polystyrene standards areprepared at 0.025 g in 50 mL of solvent for molecular weights equal toor greater than 1,000,000 and 0.05 g in 50 mL of solvent for molecularweights less than 1,000,000. The polystyrene standards were dissolved at80° C. with gentle agitation for 30 minutes. The narrow standardmixtures are run first and in order of decreasing amount of the highestmolecular weight component to minimize degradation. The polystyrenestandard peak molecular weights are converted to polyethylene molecularweights using Equation 2 (as described in Williams and Ward, J. Polym.Sci., Polym. Let., 6, 621 (1968)):M _(polyethylene) =A×(M _(polystyrene))^(B)  (Eq. 2),where M is the molecular weight of polyethylene or polystyrene (asmarked), and B is equal to 1.0. It is known to those of ordinary skillin the art that A may be in a range of about 0.38 to about 0.44 and isdetermined at the time of calibration using a broad molecular weightdistribution polyethylene standard, as outlined in the gpcBR BranchingIndex by 3D-GPC method, infra, and specifically Equation 9. Use of thispolyethylene calibration method to obtain molecular weight values, suchas M_(w)/M_(n), and related statistics, is defined here as the method ofWilliams and Ward.

The systematic approach for the determination of multi-detector offsetsis performed in a manner consistent with that published by Balke,Mourey, et al. (Mourey and Balke, Chromatography Polym., Chapter 12,(1992)) (Balke, Thitiratsakul, Lew, Cheung, Mourey, ChromatographyPolym., Chapter 13, (1992)), optimizing triple detector log (M_(w) andintrinsic viscosity) results from Dow 1683 broad polystyrene (AmericanPolymer Standards Corp.; Mentor, Ohio) or its equivalent to the narrowstandard column calibration results from the narrow polystyrenestandards calibration curve. The molecular weight data is obtained in amanner consistent with that published by Zimm (Zimm, B. H., J. Chem.Phys., 16, 1099 (1948)) and Kratochvil (Kratochvil, P., Classical LightScattering from Polymer Solutions, Elsevier, Oxford, N.Y. (1987)). Theoverall injected concentration used in the determination of themolecular weight is obtained from the mass detector area and the massdetector constant derived from a suitable linear polyethylenehomopolymer, or one of the polyethylene standards of known weightaverage molecular weight. The calculated molecular weights are obtainedusing a light scattering constant derived from one or more of thepolyethylene standards mentioned and a refractive index concentrationcoefficient, do/dc, of 0.104. Generally, the mass detector response andthe light scattering constant should be determined from a linearstandard with a molecular weight in excess of about 50,000 daltons. Theviscometer calibration can be accomplished using the methods describedby the manufacturer or alternatively by using the published values ofsuitable linear standards such as Standard Reference Materials (SRM)1475a, 1482a, 1483, or 1484a. The chromatographic concentrations areassumed low enough to eliminate addressing 2^(nd) viral coefficienteffects (concentration effects on molecular weight).

gpcBR Branching Index by 3D-GPC: In the 3D-GPC configuration, thepolyethylene and polystyrene standards can be used to measure theMark-Houwink constants, K and α, independently for each of the twopolymer types, polystyrene and polyethylene. These can be used to refinethe Williams and Ward polyethylene equivalent molecular weights inapplication of the following methods.

The gpcBR branching index is determined by first calibrating the lightscattering, viscosity, and concentration detectors as describedpreviously. Baselines are then subtracted from the light scattering,viscometer, and concentration chromatograms. Integration windows arethen set to ensure integration of all of the low molecular weightretention volume range in the light scattering and viscometerchromatograms that indicate the presence of detectable polymer from therefractive index chromatogram. Linear polyethylene standards are thenused to establish polyethylene and polystyrene Mark-Houwink constants asdescribed previously. Upon obtaining the constants, the two values areused to construct two linear reference conventional calibrations forpolyethylene molecular weight and polyethylene intrinsic viscosity as afunction of elution volume, as shown in Equations 3 and 4:

$\begin{matrix}{{M_{PE} = {\left( \frac{K_{PS}}{K_{PE}} \right)^{{1/\alpha_{PE}} + 1} \cdot M_{PS}^{\alpha_{PS} + {1/\alpha_{PE}} + 1}}},{and}} & \left( {{Eq}.\mspace{14mu} 3} \right) \\{\lbrack\eta\rbrack_{PE} = {K_{PS} \cdot {M_{PS}^{\alpha + 1}/{M_{PE}.}}}} & \left( {{Eq}.\mspace{11mu} 4} \right)\end{matrix}$

The gpcBR branching index is a robust method for the characterization oflong chain branching as discussed in Yau, Wallace W., “Examples of Using3D-GPC—TREF for Polyolefin Characterization”, Macromol. Symp., 2007,257, 29-45. The index avoids the slice-by-slice 3D-GPC calculationstraditionally used in the determination of g′ values and branchingfrequency calculations in favor of whole polymer detector areas. From3D-GPC data, one can obtain the sample bulk absolute weight averagemolecular weight (M_(w, Abs)) by the light scattering (LS) detectorusing the peak area method. The method avoids the slice-by-slice ratioof light scattering detector signal over the concentration detectorsignal as required in a traditional g′ determination.

With 3D-GPC, absolute weight average molecular weight (“M_(w, Abs)”) andintrinsic viscosity are also obtained independently using Equations 5and 6:

$\begin{matrix}\begin{matrix}{M_{W} = {\sum\limits_{i}{w_{i}M_{i}}}} \\{= {\sum\limits_{i}{\left( \frac{C_{i}}{\sum\limits_{i}C_{i}} \right)M_{i}}}} \\{= \frac{\sum\limits_{i}{C_{i}M_{i}}}{\sum\limits_{i}C_{i}}} \\{= \frac{\sum\limits_{i}{LS}_{i}}{\sum\limits_{i}C_{i}}} \\{= \frac{{LS}\mspace{14mu}{Area}}{{Conc}.\mspace{11mu}{Area}}}\end{matrix} & \left( {{Eq}.\mspace{14mu} 5} \right)\end{matrix}$The area calculation in Equation 5 offers more precision because as anoverall sample area it is much less sensitive to variation caused bydetector noise and GPC settings on baseline and integration limits. Moreimportantly, the peak area calculation is not affected by the detectorvolume offsets. Similarly, the high-precision sample intrinsic viscosity(IV) is obtained by the area method shown in Equation 6:

$\begin{matrix}\begin{matrix}{{IV} = \lbrack\eta\rbrack} \\{= {\sum\limits_{i}{w_{i}{IV}_{i}}}} \\{= {\sum\limits_{i}{\left( \frac{C_{i}}{\sum\limits_{i}C_{i}} \right){IV}_{i}}}} \\{= \frac{\sum\limits_{i}{C_{i}{IV}_{i}}}{\sum\limits_{i}C_{i}}} \\{= \frac{\sum\limits_{i}{DP}_{i}}{\sum\limits_{i}C_{i}}} \\{{= \frac{{DP}\mspace{14mu}{Area}}{{Conc}.\mspace{14mu}{Area}}},}\end{matrix} & \left( {{Eq}.\mspace{14mu} 6} \right)\end{matrix}$where DP_(i) stands for the differential pressure signal monitoreddirectly from the online viscometer.

To determine the gpcBR branching index, the light scattering elutionarea for the sample polymer is used to determine the molecular weight ofthe sample. The viscosity detector elution area for the sample polymeris used to determine the intrinsic viscosity (IV or [η]) of the sample.

Initially, the molecular weight and intrinsic viscosity for a linearpolyethylene standard sample, such as SRM1475a or an equivalent, aredetermined using the conventional calibrations (“cc”) for both molecularweight and intrinsic viscosity as a function of elution volume, perEquations 7 and 8:

$\begin{matrix}{{{Mw}_{CC} = {{\sum\limits_{i}{\left( \frac{C_{i}}{\sum\limits_{i}C_{i}} \right)M_{i}}} = {\sum\limits_{i}{w_{i}M_{{cc},i}}}}},{and}} & \left( {{Eq}.\mspace{14mu} 7} \right) \\{\lbrack\eta\rbrack_{CC} = {{\sum\limits_{i}{\left( \frac{C_{i}}{\sum\limits_{i}C_{i}} \right){IV}_{i}}} = {\sum\limits_{i}{w_{i}{{IV}_{{cc},i}.}}}}} & \left( {{Eq}.\mspace{14mu} 8} \right)\end{matrix}$Equation 9 is used to determine the gpcBR branching index:

$\begin{matrix}{{{{gpc}\;{BR}} = \left\lbrack {{\left( \frac{\lbrack\eta\rbrack_{CC}}{\lbrack\eta\rbrack} \right) \cdot \left( \frac{M_{W}}{M_{W,{CC}}} \right)^{\alpha_{PE}}} - 1} \right\rbrack},} & \left( {{Eq}.\mspace{14mu} 9} \right)\end{matrix}$wherein [η] is the measured intrinsic viscosity, [η]_(cc) is theintrinsic viscosity from the conventional calibration, M_(w) is themeasured weight average molecular weight, and M_(w,cc) is the weightaverage molecular weight of the conventional calibration. The weightaverage molecular weight by light scattering (LS) using Equation (5) iscommonly referred to as “absolute weight average molecular weight” or“M_(w, Abs)”. The M_(w,cc) from Equation (7) using conventional GPCmolecular weight calibration curve (“conventional calibration”) is oftenreferred to as “polymer chain backbone molecular weight”, “conventionalweight average molecular weight”, and “M_(w,GPC)”.

All statistical values with the “cc” subscript are determined usingtheir respective elution volumes, the corresponding conventionalcalibration as previously described, and the concentration (C_(i))derived from the retention volume molecular weight calibration. Thenon-subscripted values are measured values based on the mass detector,LALLS, and viscometer areas. The value of K_(PE) is adjusted iterativelyuntil the linear reference sample has a gpcBR measured value of zero.For example, the final values for α and Log K for the determination ofgpcBR in this particular case are 0.725 and −3.355, respectively, forpolyethylene, and 0.722 and −3.993 for polystyrene, respectively.

Once the K and α values have been determined using the procedurediscussed previously, the procedure is repeated using the branchedsamples. The branched samples are analyzed using the final Mark-Houwinkconstants as the best “cc” calibration values and Equations 5-8 areapplied.

The interpretation of gpcBR is as follows: For linear polymers, gpcBRcalculated from Equation 9 will be close to zero since the valuesmeasured by LS and viscometry will be close to the conventionalcalibration standard. For branched polymers, gpcBR will be higher thanzero, especially with high levels of long chain branching, because themeasured polymer molecular weight will be higher than the calculatedM_(w,cc), and the calculated IV_(cc) will be higher than the measuredpolymer IV. In fact, the gpcBR value represents the fractional IV changedue the molecular size contraction effect as the result of polymerbranching. A gpcBR value of 0.5 or 2.0 would mean a molecular sizecontraction effect of IV at the level of 50% and 200%, respectively,versus a linear polymer molecule of equivalent weight.

For these particular Examples, the advantage of using gpcBR incomparison to a traditional “g′ index” and branching frequencycalculations is due to the higher precision of gpcBR. All of theparameters used in the gpcBR index determination are obtained with goodprecision and are not detrimentally affected by the low 3D-GPC detectorresponse at high molecular weight from the concentration detector.Errors in detector volume alignment also do not affect the precision ofthe gpcBR index determination.

Zero Shear Viscosity: Specimens for creep measurements were prepared ona programmable Tetrahedron bench top press. The program held the melt at177° C. for 5 minutes at a pressure of 10⁷ Pa. The chase was thenremoved to the bench to cool down to room temperature. Round testspecimens were then die-cut from the plaque using a punch press and ahandheld die with a diameter of 25 mm. The specimen is about 1.8 mmthick.

Zero-shear viscosities are obtained via creep tests that were conductedon an AR-G2 stress controlled rheometer (TA Instruments; New Castle,Del.) using 25-mm-diameter parallel plates at 190° C. Two thousand ppmof antioxidant, a 2:1 mixture of IRGAFOS 168 and IRGANOX 1010 (CibaSpecialty Chemicals; Glattbrugg, Switzerland), is added to stabilizeeach sample prior to compression molding. The rheometer oven is set totest temperature of 190° C. for at least 60 minutes prior to zeroingfixture. At the testing temperature a compression molded sample disk isinserted between the plates and allowed to come to equilibrium for 5minutes. The upper plate is then lowered down to 50 μm above the desiredtesting gap (1.5 mm). Any superfluous material is trimmed off and theupper plate is lowered to the desired gap. Measurements are done undernitrogen purging at a flow rate of 5 L/min. The default creep time isset for 6 hours.

A low shear stress of 5 to 20 Pa is applied for all of the samples toensure that the steady state shear rate is low enough to be in theNewtonian region. Steady state is determined by taking a linearregression for all the data in the last 10% time window of the plot oflog(J(t)) vs. log(t), where J(t) is creep compliance and t is creeptime. If the slope of the linear regression is greater than 0.97, steadystate is considered to be reached, then the creep test is stopped. Inall cases in this study the samples reached steady state within 6 hours.The steady state shear rate is determined from the slope of the linearregression of all of the data points in the last 10% time window of theplot of ε vs. t, where ε is strain. The zero-shear viscosity isdetermined from the ratio of the applied stress to the steady stateshear rate.

A dynamic oscillatory shear test is conducted before and after the creeptest on the same specimen from 0.1 to 100 rad/s at 10% strain. Thecomplex viscosity values of the two tests are compared. If thedifference of the viscosity values at 0.1 rad/s is greater than 5%, thesample is considered to have degraded during the creep test, and theresult is discarded.

Total Sulfur Concentration: The total concentration of sulfur found inthe ethylene-based polymer product—both molecularly bonded to theethylene-based polymer and “free” sulfur (i.e., sulfur contained inbyproduct and other compounds homogeneously incorporated with theethylene-based polymer)—is determined by X-ray fluorescence (XRF) usingan Axios-Petro X-ray fluorescence (XRF) spectrometer with a Rh tube fromPANalytical GmbH (Kassel-Waldau, Germany). The XRF spectrometer iscalibrated by using a standard of 1000 μs/kg S in mineral oil (Cat. No.ORG-S8-2Z; Spex Certiprep; Metuchen, N.J.) and clean oil (Standard oil;Merck KGaA, Darmstadt, Germany). It is understood that the letter “S” inthis instance refers to elemental sulfur. The XRF-method has a sulfurdetection threshold of 5 ppm by weight based upon the brutto intensitiesof the standards. All standards and samples were measured in sample cupscovered with a polypropylene-based film. For each measurement,approximately 3 g of ethylene-based polymer is hot pressed into a 31 mmdiameter disk, resulting in a specimen about 4 mm thick. The sampledisks are then secured in the center of the sample cup with a centeringring for testing. The XRF spectrometer is set to the conditions listedin Table 1 for each test and the test performed.

TABLE 1 XRF spectrometer conditions for each Total Sulfur Concentrationtest. Attribute Setting Channel S Line KA Crystal Ge 111-C Collimator300 μm Collimator mask  27 mm Detector Flow Tube filter Be (150 μm) kV25 mA 96 Angle (°2T) 110.6620 Offset Background1 (°2T) 1.0000 OffsetBackground2 (°2T) −1.6000 Measurement time 10 s (for each channel)Background method Calculated factors

The background corrected intensities were exported into the matrixcorrection program “Personal Computer Fundamental Parameters forWindows” by Fundex Software and Technology, Inc. (Northridge, Calif.). Alinear calibration curve based upon sulfur concentration is determinedfrom the intensity responses from the oil and sulfur standards. Thelinear calibration curve is used to calculate the total sulfurconcentration in each sample. The composition of the floater was set toC₁H₂.

Surface and Internal Haze: Samples measured for internal haze andoverall haze are sampled and prepared according to ASTM D 1003. AHazegard Plus (BYK-Gardner USA; Columbia, Md.) is used for testing.Surface haze is determined as the difference between overall haze andinternal haze. Surface haze tends to be related to the surface roughnessof the film, where surface haze increases with increasing surfaceroughness. The surface haze to internal haze ratio is the surface hazevalue divided by the internal haze value.

Blown Film Fabrication Conditions: The sample films are extrusion blownfilms produced on a 45 mm COVEX Monolayer Blown Film Line (Barcelona,Spain) using the conditions in Table 2.

TABLE 2 Extrusion blown film processing conditions for producing samplesused in Surface and Internal Haze tests. Variable Unit Value AirTemperature at cooling ring ° C. 23 Amps A 23 Average Thickness Um 50B.U.R. (Blow Up Ratio) — 2.5 Die gap Mm 1 Frost line height Mm 300Layflat Mm 584 Line Speed m/min 9.5 Melt Pressure, Adapter Bar 0 MeltPressure, Barrel Bar 203 Melt Temperature, Adapter ° C. 213 MeltTemperature, Barrel ° C. 194 Output Rate kg/h 29 RPM Rpm 77 Volts V 250

GPC-LS Characterization: Analysis of a concentration-normalized LSchromatogram response curve for a particular sample using apre-determined molecular weight range is useful in differentiating theembodiment polymers from analogous and commercially availablecomparative low density ethylene-based polymers. The “GPC-LSCharacterization” parameter, Y, is designed to capture the uniquecombination of molecular weight distribution (MWD) and the GPC-LSprofile for a specific material. The properties of interest are meltindex (I₂), MWD, long chain branching, and haze. Desirable attributesfor a polymer with a low haze are higher melt index (I₂), narrower MWD,and lower long chain branching values. All in all, the GPC-LSCharacterization value is designed to capture the features of low longchain branching, narrow MWD, and high melt index (I₂). FIG. 2 providesan example and guide for using the GPC-LS Characterization method toidentify inventive embodiments.

An ethylene-based polymer that has long chain branching, such a lowdensity ethylene-based polymers, can be differentiated by using ananalysis technique called “GPC-LS Characterization”. In the GPC-LSCharacterization method, the determination is made using the lightscattering (LS) detector response for a sample processed by aconventionally calibrated 3D-GPC (“cc-GPC”) over a range of molecularweights of the sample. The molecular weights of the sample are convertedto logarithm values for scaling purposes. The LS response is“concentration-normalized” so the LS response can be compared betweensamples, as it is known in the art that the unnormalized LS signals canvary greatly from sample to sample without normalization. When plotted,the logarithm values of range of the cc-GPC molecular weights and theconcentration-normalized LS values form a concentration-normalized LSchromatogram curve such as the one shown in FIG. 2.

Once the concentration-normalized LS chromatogram curve is available,the determination of the GPC-LS Characterization value isstraightforward. In the GPC-LS Characterization method, a GPC-LSCharacterization value (Y) is determined using the following equation:Y=(0−x)*(A/B)  (Eq. 10).Essentially, the GPC-LS Characterization value is a relationship betweentwo associated areas (A and B) and an indexed slope of a line (x)between two points on the concentration-normalized LS chromatogram curveat the logarithmic values of two specified cc-GPC molecular weightvalues. The specified cc-GPC molecular weight values attempt to bracketa molecular weight fraction that is known to contain polymer chains withlong chain branching.

The first step in the analysis is generation of theconcentration-normalized LS chromatogram curve representingconcentration-normalized LS response values versus the logarithmicvalues of cc-GPC molecular weights for the polymer being examined.

The second step is to draw a straight line between two points on theconcentration-normalized LS chromatogram curve. The straight line andthe points will provide the basis for determination of areas A and B.The two points, a first point and a second point, are located on theconcentration-normalized LS chromatogram curve and represent theconcentration-normalized LS response values (a first and a secondconcentration-normalized LS response values) at the logarithm values fortwo cc-GPC molecular weight values (a first and a second logarithmiccc-GPC molecular weight values). The first point (Point 1 on FIG. 2) isdefined as being on the concentration-normalized LS chromatogram curve(representing the first concentration-normalized LS response value)corresponding to the logarithm value of cc-GPC molecular weight 350,000grams/mole (representing the first logarithmic cc-GPC molecular weightvalue), which is a value of approximately 5.54. The second point (Point2 on FIG. 2) is defined as being along the concentration-normalized LSchromatogram curve at the concentration-normalized LS response value(representing the second concentration-normalized LS response value)corresponding to a logarithm value of cc-GPC molecular weight 1,150,000grams/mole (representing the second logarithmic cc-GPC molecular weightvalue), which is a value of approximately 6.06. It is known in the artthat differentiation in long chain branching typically is shown around1M grams/mole cc-GPC molecular weight.

The third step is to determine the area A between the straight line andthe concentration-normalized LS chromatogram curve between the twologarithmic cc-GPC molecular weight values. Area A is defined as beingthe value of A1 minus A2. In preferred embodiments, the area A isdefined for the range of values between the logarithm value of cc-GPCmolecular weight 350,000 grams/mole and the logarithm value of cc-GPCmolecular weight 1,150,000 grams/mole.

A1 is defined as the area bound between the straight line and thenormalized LS chromatogram curve where the concentration-normalized LSresponse value of the straight line is greater than theconcentration-normalized LS response value for theconcentration-normalized LS chromatogram curve between the twologarithmic cc-GPC molecular weight values.

As can be seen in FIG. 2, the area defined as A1 fills the entire rangebetween the two logarithmic cc-GPC molecular weights; therefore A=A1. Inmany cases the straight line will be “above” theconcentration-normalized LS chromatogram curve for the logarithmiccc-GPC molecular weight range and will not intersect with theconcentration-normalized LS chromatogram curve except at Points 1 and 2.In these cases, A=A1 and A2=0. In some embodiments, however, A is notequal to A1. The concentration-normalized LS chromatogram curve shown inFIG. 3 shows an example of when this may occur.

In some embodiments, as can be seen in FIG. 3, the straight line mayintersect with the concentration-normalized LS chromatogram curve in atleast one other point besides Points 1 and 2 (see FIG. 3 at “StraightLine Intersection”). In such situations, A1 is determined as previouslydefined. For the example shown in FIG. 3, A1 would be the area betweenthe concentration-normalized LS chromatogram curve and the straight linebetween the logarithm cc-GPC molecular weight value of approximately 5.8to the logarithm value of cc-GPC molecular weight 1,150,000 grams/mole.

A2 is defined as the inverse of A1. A2 is the area bound between thestraight line and the concentration-normalized LS chromatogram curvewhere the concentration-normalized LS response of the straight line isless than the concentration-normalized LS response for theconcentration-normalized LS chromatogram curve between the twologarithmic cc-GPC molecular weight values. For the example shown inFIG. 3, A2 is the area between the concentration-normalized LS responsecurve and the straight line between the logarithm cc-GPC molecularweight value of approximately 5.8 to the logarithm value of cc-GPCmolecular weight 350,000 grams/mole.

In calculating a total value for A, A is again defined as the area A1minus the area A2. In some embodiments, as can be seen graphically inFIG. 3, A may result in a negative value, reflecting that the straightline defines more of an area below the concentration-normalized LSresponse curve than above it.

The fourth step is to determine the area B under theconcentration-normalized LS chromatogram curve for the logarithmiccc-GPC molecular weight range. B is defined as the area under theconcentration-normalized LS chromatogram curve between the twologarithmic cc-GPC molecular weight values. Area B does not depend uponthe analysis of area A.

The fifth step is to determine the value of x, the slope indexing value.The value of the x is an indexing factor that accounts for the slope ofthe straight line established for determining areas A and B. The valueof x is not the slope of the straight line; however, it does represent avalue reflective of the difference between Points 1 and 2. The value ofx is defined by Equation 11:

$\begin{matrix}{{x = \frac{\frac{{LSresponse}_{({{{Point}\; 2},{CN}})} - {LSresponse}_{({{{Point}\; 1},{CN}})}}{{LSresponse}_{({{{Point}\; 2},{CN}})}}}{{\log\;{MW}_{({{{Point}\; 2},{ccGPC}})}} - {\log\;{MW}_{({{{Point}\; 1},{ccGPC}})}}}},} & \left( {{Eq}.\mspace{14mu} 11} \right)\end{matrix}$where “LS response” are the concentration-normalized LS response valuesfor Points 1 and 2, respectively, and “log MW” are the logarithmiccc-GPC molecular weights for Points 1 and 2, respectively. In preferredembodiments, the value of x is negative, indicating the straight line isdownward sloping. In some embodiments, the straight line may intersectthe normalized LS chromatogram curve at least once between Points 1 and2.

Finally, once x, A, and B are established, the GPC-LS Characterizationvalue (Y) is determined using the previously presented Equation 10:Y=(0−x)*(A/B)  (Eq. 10).

When examining a LS chromatogram response curve, it is known that thesize of the LS peak at about log MW 6 is related to the level of longchain branching in the polymer. The smaller the log MW 6 LS peak is, thevalue of the slope of the line segment in the LS plot becomes morenegative because the line is more steeply angled. This results in a morenegative indexed slope of a line (x) value. A more negative x-valuecontributes to a higher positive value of Y, given the relationship inEquation 10.

The other term that contributes to Y in Equation 10 is the area ratio ofA/B. The higher the A/B ratio gives, the higher the Y value. This ratiois affected by the melt index (I₂) and the MWD values of the polymer.These two values in turn affect how far the main polymer peak is pulledaway from the LS pre-peak near the Log MW of 6 high MW region. A highermelt index (I₂) value means a lower MW, indicating a more distinctseparation between the two response peaks. This would create a deepervalley between the high and low MW fractions. A deeper valley creates alarger area beneath the line segment, designated as “A”. A narrow MWDmeans a less broad LS response curve and has the similar effect ofcreating a deeper valley in the plot, and again a larger area A.

Extrusion Multi-pass: A relative measurement of atmospheric stability(that is, resistance to oxidative attack and degradation) of two or moreresins may be tested by passing polymer samples through a heatedextruder several times under atmospheric conditions and then testing forphysical characteristics such as melt index (I₂) after each pass.

The polymer samples are processed through a LEISTRIZ micro-18 twin-screwextruder (obtained from American Leistritz Extruder Corporation,Somerville, N.J.). The extruder is controlled and driven by a HAAKE™PolyLab System (Thermo Fischer Scientific; Waltham, Mass.) computersystem. The extruder consists of 6 heating zones of 90 mm length each,and a heated die with a 3 mm strand orifice. The first zone is the feedthroat and is jacket cooled with flowing water to prevent bridging ofthe feed polymer. The first zone is equipped with an open cone toreceive the polymer feed from a K-TRON KV2T20 twin auger feeder (Pitman,N.J.). The five heated zones are set at 135, 165, 200, 220, and 220° C.,respectively. The die at the end of the extruder is heated to 220° C.

Each screw has a diameter of 18 mm and a length of 540 mm, resulting inan L/D ratio of 30. The screw stack for the first five zones consists ofan open forwarding design with a 30 degree pitch (off vertical). Thefinal zone of the screw stack is a slightly narrower pitched forwardingdesign with a pitch of 20 degrees (off vertical). The overall screwdesign imparts little shear to the polymer and primarily forwards thematerial through the heated barrel sections. The molten polymer iscompressed near the end of the screw through the tighter pitched elementto provide enough back pressure to force the molten material through thedie.

When processing, the screws turns at 250 rotations per minute (rpm). Thepolymer is fed to the extruder by the feeder with enough polymer toprocess as many passes as necessary while permitting the acquisition ofa sample, preferably about 50 grams, after each pass for analysis.

The resultant molten polymer strand is delivered into a chilled waterbath where it solidifies. After solidification, the polymer strandpasses through an air knife to remove water before being cut by a strandchopper into polymer pellets. Upon pellitization, the sample foranalysis is obtained before returning the remainder back into the feederfor additional processing if necessary.

EXAMPLES

The invention is further illustrated by means of the following,non-limiting examples. In discussing the Examples and ComparativeExamples, several terms are defined. There are two Example compositionsand sets of process information for their creation: Example 1 andExample 2. There are three Comparative Examples compositions and sets ofprocess information. The process runs that created Comparative Examples1, 2, and 3 are analogous in that they are produced using the sameprocess train as Examples 1 and 2. Comparative Examples 1 and 2 aredirectly comparative with Examples 1 and 2, respectively. The disclosedinformation regarding Comparative Example 3 is generally comparative inthat the conditions are similar, but not comparative, to both Examples 1and 2, and the process is analogous (same process train). Processinformation on Comparative Examples 1, 2, and 3 are available infra.

In addition to Comparative Examples 1-3, several “commercial”Comparative Examples (Comparative Examples 4, 5, 6, et seq.) are alsoused for comparison purposes related to material properties.“Commercial” comparative examples, as they may sometimes be referred to,are LDPE materials that are generally available “off the shelf” and arecommercially sold or are grades of LDPE that have been produced in smallquantities in a laboratory that, if properly scaled up, could beproduced and sold commercially.

When process conditions are discussed and compared, the processconditions may be referred to by their product designation (e.g.,process conditions for producing Example 1 product may be referred to as“the process of Example 1”).

Examples 1 and 2 as well as Comparative Examples 1, 2, and 3 areproduced on the same process reaction system; therefore, in referring tothe same equipment between the runs, the physical process and its unitsare analogous to one another. FIG. 4 is a simple block diagram of theprocess reaction system 200 used to produce the aforementioned Examplesand Comparative Examples.

Process reaction system 200 in FIG. 4 is a partially closed-loop dualrecycle high-pressure, low density polyethylene production system.Process reaction system 200 is comprised of a fresh ethylene feedconduit 206; parallel primary compressors 204A and 204B; hypercompressor205, which is made up of two parallel hypercompressors 205A and 205B,each further comprised of a first compression stage and a secondcompression stage with intercoolers 205C in-between each compressionstage; a tube reactor 202; a first reaction zone feed conduit 212; adownstream reaction zones feed conduit 214; a first peroxide initiatorconduit 207 connected to a first peroxide initiator source 247; a secondperoxide initiator conduit 287 connected to the first peroxide initiatorsource 247; a third peroxide initiator conduit 217 connected to a secondperoxide initiator source 257; first (230), second (231), and third(232) cooling jackets (using water) mounted around the outer shell ofthe tube reactor 202; a preheater 235 mounted around the outer shell atthe front of the tube reactor 202; a high pressure separator 218; a highpressure recycle line 226; a high pressure recycle system 224; a lowpressure separator 220; a low pressure recycle line 208; a boostercompressor 221; and a CTA feed conduit 223 connected to a CTA feedsource 253.

Tube reactor 202 further comprises three reaction zones demarcated bythe location of peroxide injection points. Tube reactor 202 has a lengthof about 1540 meters. The first reaction zone feed conduit 212 isattached to the front of the tube reactor 202 at 0 meters and feeds aportion of the process fluid into the first reaction zone. The firstreaction zone starts at injection point #1 (271), which is located about120 meters downtube of the front of the tube reactor 202 and ends atinjection point #2 (272). The first peroxide initiator conduit 207 isconnected to the tube reactor 202 at injection point #1 (271). Thesecond reaction zone starts at injection point #2 (272), which is about520 meters downtube from the front of the tube reactor 202. A branchfrom the downstream reaction zones feed conduit 214, feeding a portionof the process fluid directly to the second reaction zone, and thesecond peroxide initiator conduit 287 are connected to the tube reactor202 at injection point #2 (272). The second reaction zone ends atinjection point #3 (273). The third reaction zone starts at injectionpoint #3 (273), which is located about 980 meters downtube from thefront of the tube reactor 202. A branch from the downstream reactionzones feed conduit 214 is connected slightly uptube—about 10 meters—frominjection point #3 (273) and feeds a portion of the process fluid to thethird reaction zone.

The preheater 235 and the first reaction zone of the tube reactor 202have a diameter of 4 centimeters. The second reaction zone of the tubereactor 202 has a diameter of 6 centimeters. The third reaction zone ofthe tube reactor 202 has a diameter of 6 centimeters.

For all the Examples and the Comparative Examples 1-3, approximately 50%of the process fluid is directed to the first reaction zone via thefirst reaction zone feed conduit 212. Approximately 35% of the processfluid is directed to the second reaction zone via the downstreamreaction zones feed conduit 214. The remaining process fluid is directedto the third reaction zone via the downstream reaction zones feedconduit 214.

For all the Examples and the Comparative Examples 1-3, a mixturecontaining t-butyl peroxy-2 ethylhexanoate (TBPO), di-t-butyl peroxide(DTBP), and an n-paraffin hydrocarbon solvent (180-240° C. boilingrange) is used as the initiator mixture for the first (271) and second(272) injection points. For injection point #3 (273), a mixturecontaining DTBP and the n-paraffin hydrocarbon solvent is used. Table 3shows the weight of the peroxide initiator solution used for each of thetrial runs.

TABLE 3 Peroxide initiator mass flow rates in kilograms per hour at eachinjection point used to produce the Examples 1-2 and ComparativeExamples 1-3. Organic peroxide Comparative Comparative Comparative (PO)Example 1 Example 1 Example 2 Example 2 Example 3 Injection LocationMaterial (kg/hr) (kg/hr) (kg/hr) (kg/hr) (kg/hr) Injection Point #1 TBPO0.89 0.86 0.89 0.87 0.86 Injection Point #1 DTBP 0.37 0.36 0.38 0.370.36 Injection Point #2 TBPO 1.30 1.35 1.69 1.69 1.22 Injection Point #2DTBP 0.55 0.57 0.71 0.71 0.52 Injection Point #3 TBPO 0.00 0.00 0.000.00 0.00 Injection Point #3 DTBP 0.63 0.64 0.79 0.78 0.59

For Examples 1 and 2, a blend of two chain transfer agents—one CTA witha Cs less than one (propionaldehyde or “PA”) and one CTA with a Csgreater than one (tert-dodecyl mercaptan or “TDM”)—are injected into theprocess fluid at the inlet of parallel hypercompressor 205A. The TDM isSulfole® 120 Mercaptan from Chevron Philips Chemical Co. of TheWoodlands, Texas. When using more than one CTA in the disclosed process,the CTAs are pumped individually and mixed together inline. By being fedinto the inlet of parallel hypercompressors 205A, the CTA mixtures forExamples 1 and 2 are fed only to the front of the tube reactor 202 viafirst reaction zone feed conduit 212. Comparative Examples 1 and 2 arealso “front fed” to the tube reactor 202 in the same manner; however,only PA is fed during those process runs. Comparative Example 3, likeComparative Examples 1 and 2, only uses PA as its chain transfer agent,but the process of Comparative Example 3 does not feed the entire amountof CTA to the front of the tube reactor 202. Although not shown in FIG.4, a portion of the CTA feed for Comparative Example 3 is fed to thesecond and third reaction zones. This is accomplished by injecting aportion of the CTA feed to the inlet of parallel hypercompressors 205B.As previously discussed, the process fluid discharge of parallelhypercompressor 205B is fed into the second and third reaction zonesusing the downstream reaction zones feed conduit 214.

The amounts and compositions of the CTA feeds to the comparativeprocesses are the only control variables changed between the comparativeprocess runs of Examples 1 and 2 and Comparative Examples 1 and 2. Theother controlled process variables are set at comparable values for thefour runs.

Table 4 shows the amounts and composition of the chain transfer agentsthat are used in the disclosed process.

TABLE 4 Chain transfer agent mass flow rates for Examples 1 and 2 andComparative Examples 1, 2, and 3. Note that “Front Feed” refers to theCTAs being fed to the reactor tube via the first reaction zone feedconduit and that “Downstream Feed” refers to the CTAs being fed to thereactor tube via the downstream reaction zones feed conduit. ComparativeComparative Comparative Chain Transfer Agent Example 1 Example 1 Example2 Example 2 Example 3 Addition Location (kg/hr) (kg/hr) (kg/hr) (kg/hr)(kg/hr) CTA-types PA + TDM PA PA + TDM PA PA PA - Front Feed 15.5 22.615.1 23.0 19.5 PA - Downstream Feed 0.0 0.0 0.0 0.0 4.0 TDM - Front Feed14.0 0.0 14.0 0.0 0.0 TDM - Downstream Feed 0.0 0.0 0.0 0.0 0.0

The mass flow rate, in kg/hour, of the chain transfer agents into thetube reactor 202 depends on many factors, such as expense andsolubility, but most notably the relative chain transfer constants ofthe two or more CTAs. For example, in Example 1 and 2, the mass flowrate of the chain transfer agent having a Cs greater than 1 (TDM) islower than the mass flow rate of the chain transfer agent having a Csgreater than 1 (PA).

The molar flow rate, in kg/mol, of a chain transfer agent is related tothe mass flow rate by taking the mass flow rate of the CTA and dividingby the CTA's molecular weight in kg/mol. For example, the molecularweight of PA is 0.058 kg/g-mol. The molecular weight of TDM is 0.201kg/g-mol.

The reactor tube process conditions used to manufacture Examples 1 and 2and Comparative Examples 1, 2, and 3 are given in Table 5.

TABLE 5 Production conditions and results for Examples 1 and 2 andComparative Examples 1, 2, and 3. Note that “CJW” means “cooling jacketwater”. Comparative Comparative Comparative Trial Run Units Example 1Example 1 Example 2 Example 2 Example 3 Reactor Inlet Pressure Bar 23312329 2330 2330 2320 Reaction Zone 1 - Initiation Temperature ° C. 140.0140.0 140.0 140.0 145.0 Reaction Zone 1 - Peak Temperature ° C. 284.7285.1 286.8 287.1 287.7 Reaction Zone 1 - Outlet Temperature ° C. 201.4204.6 201.7 205.2 203.4 Downstream Process Fluid Temperature ° C. 70.365.9 69.1 64.1 67.7 Reaction Zone 2 - Initiation Temperature ° C. 150.1149.8 150.0 149.9 150.0 Reaction Zone 2 - Peak Temperature ° C. 290.4290.2 295.6 295.3 287.3 Reaction Zone 2 - Outlet Temperature ° C. 228.8230.5 231.3 232.5 229.5 Reaction Zone 3 - Initiation Temperature ° C.211.2 214.0 213.5 214.9 213.0 Reaction zone 3 - Peak Temperature ° C.290.2 289.7 295.1 294.6 288.0 Inlet Water Temperature - CJW ° C. 168.6168.6 168.9 168.9 168.7 Delta T - CJW - Reaction Zone 1 ° C. 21.4 20.921.3 20.9 21.7 Delta T - CJW - Reaction Zone 2 ° C. 23.1 23.0 24.4 24.022.2 Delta T - CJW - Reaction Zone 3 ° C. 10.8 10.8 10.8 10.8 10.7 Flowrate - CJW - Reaction Zone 1 MT/hr 100 100 100 100 100 Flow rate - CJW -Reaction Zone 2 MT/hr 120 120 120 120 120 Flow rate - CJW - ReactionZone 3 MT/hr 210 210 210 210 210 Fresh Ethylene Feed MT/hr 15.6 15.416.1 15.9 15.2 Ethylene Throughput in Tube Reactor MT/hr 55.7 56.0 55.956.1 56.0 Ethylene Conversion % 27.7 27.3 28.4 28.0 26.9 PolyethyleneProduction Rate MT/hr 15.4 15.3 15.9 15.7 15.0

It can be observed from the data given in Table 5 that evidence existsof the effects of the suppression of high-molecular weight polymerchains early in the process due to the presence of the high-Cs chaintransfer agents. As shown in Table 4, the high-Cs chain transfer agent,TDM, is only fed to the process—and only to the front part of theprocess—during the runs for Examples 1 and 2. At the process conditionsreported in Table 5, TDM, the high-Cs chain transfer agent, has a Csgreater than 1 but less than 100, and that of PA, the low-Cs CTA, has aCs less than 1 but greater than 0.05.

As for the process condition comparison between Example 1 andComparative Example 1, Example 2 and Comparative Example 2, it can beseen through Tables 3-5 that except for the CTA feeds and amounts, theconditions were comparable. As shown in Table 5, the process conditionsfor Examples 1 and 2 indicate suppression of high-molecular weightpolymers chains through improved processing conditions in the first andsecond reaction zones. The Comparative Examples 1 and 2 each show ahigher “Reaction Zone 1—Outlet Temperature” and lower “DeltaT—CJW—Reaction Zone 1” temperature differential versus the analogous andcomparable Example process runs. Given that the “Inlet WaterTemperature—CJW” and the “Flow rate—CJW—Reaction Zone 1” are held steadyfor all four runs, it is easy to conclude that there is better heattransfer in Reaction Zone 1 during the two Example runs than from thetwo Comparative Example runs.

The improvement in heat transfer of Reaction Zone 1 has a positiveenergy impact upon the rest of the reaction system. For all the runs,the initiation temperature for the second reaction zone is targeted tobe around 150° C. Given that the “Reaction Zone 1—Outlet Temperature” ishigher than this temperature target, the process fluid in the downstreamreaction zones feed conduit 214 is cooled before injection into thereactor tube 202 at injection point #2 (272) just enough to offset thereaction system temperature and reach the temperature target. Becausethe “Reaction Zone 1—Outlet Temperature” for each Example is relativelycooler than its analogous Comparative Example, the process fluid in thedownstream reaction zones feed conduit 214 does not have to be cooled asmuch to offset the reaction system temperature at this point to meet thetemperature target. This is seen in the “Downstream Process FluidTemperature” value, which is the temperature of the process fluidinjected into the reactor tube 202 fed through the downstream reactionzones feed conduit 214. For the Examples, this temperature value isslightly higher than the same value for the Comparative Examples becausenot as much reaction system cooling is required via injection ofadditional process fluid at injection point #2 (272) to offset thereaction system temperature to meet the 150° C. target (as is furtherillustrated by the “Reaction Zone 2—Initiation Temperature” value).

Similar improved performance is seen in the second and third reactionzones. In the second reaction zone, “Reaction Zone 2—Outlet Temperature”is lower and “Delta T—CJW—Reaction Zone 2” is higher, indicatingimproved heat transfer in the second reaction zone for the Examples overthe analogous Comparative Examples. This also leads to a lower “ReactionZone 3—Initiation Temperature” for the Examples, as the final part ofthe process fluid is injected into to the process. This results in abroader temperature differential between “Reaction Zone 3-InitiationTemperature” and “Reaction zone 3—Peak Temperature” for the Examplesover the Comparative Examples, indicating a higher amount of ethyleneconversion occurring in this zone.

The final indication regarding process improvement is the ethyleneconsumption and polyethylene production. As shown in Table 5, “FreshEthylene Feed”, “Ethylene Conversion”, and “Polyethylene ProductionRate” are all higher as a result of improved overall heat removalcapability in the tube reaction system.

Upon closer inspection of the data in Table 5, the disclosed processeswould show an even greater difference between ethylene conversion andproduction rate values if the Downstream Process Fluid Temperatures ofthe Examples and Comparative Examples were forced to be closer togetherand more comparable. Comparing Example 1 and Comparable Example 1, thedifference between the Ethylene Conversion values is 0.4%, favoringExample 1. Forcing the Downstream Process Fluid Temperature ofComparative Example 1 to be a higher temperature closer to the value forExample 1 would result in a higher Comparative Example 1 Reaction Zone3—Initiation Temperature because the temperature is not controlled,unlike the Reaction Zone 2—Initiation Temperatures. The higherinitiation temperature for the third zone of Comparative Example 1 wouldresult in a drop in the overall ethylene conversion efficiency. The sametrend would hold for Example 2 and Comparative Example 2.

Examples and Comparative Examples Characterization

3D-GPC analysis is performed on the product polymers of Examples 1 and 2and Comparative Examples 1, 2, and 3. Additionally, Comparative Example4 is a commercially available LDPE material and Linear Standard 1 is a 1MI linear polyethylene standard. These results are summarized in Tables6-8; in these tables a “GPC” subscript refers to a conventionalcalibration measurements and “abs” refers to absolute (light scattering)measurement.

TABLE 6 Conventional GPC analysis of Examples 1-2 and ComparativeExamples 1-4. M_(n, GPC) M_(w, GPC) M_(z, GPC) Sample (g/mol) (g/mol)(g/mol) (M_(w)/M_(n)), _(GPC) Example 1 15,990 79,330 186,100 4.96Comparative Example 1 14,140 81,400 207,300 5.76 Example 2 15,620 81,820195,200 5.24 Comparative Example 2 15,560 85,190 227,300 5.47Comparative Example 3 15,470 80,960 206,600 5.23 Comparative Example 415,350 97,560 270,000 6.36

TABLE 7 Absolute GPC analysis of Examples 1-2 and Comparative Examples1-4. M_(w,Abs) M_(z, Abs) Sample (g/mol) (g/mol) M_(w, Abs)/M_(w,GPC)Example 1 119,740 459,500 1.51 Comparative Example 1 121,630 489,7001.49 Example 2 127,270 534,300 1.56 Comparative Example 2 129,030506,300 1.51 Comparative Example 3 122,220 509,900 1.51 ComparativeExample 4 155,070 576,800 1.59

TABLE 8 Intrinsic viscosity and gpcBR from 3D-GPC analysis of Examples1-2 and Comparative Examples 1-4. IV_(w) IV_(z) Sample (dl/g) (dl/g)gpcBR Example 1 0.94 1.34 0.97 Comparative Example 1 0.94 1.38 0.99Example 2 0.96 1.37 1.03 Comparative Example 2 0.94 1.41 1.09Comparative Example 3 0.94 1.38 1.01 Comparative Example 4 0.99 1.491.26

From Table 6 it can be seen that both Examples 1 and 2 show a narrowerM_(w)/M_(n), ratio by conventional GPC than that of their relatedComparative Examples. The comparatively narrower M_(w)/M_(n), ratios ofboth Examples indicates that the Example materials can provide benefitsin mechanical properties as well as improved clarity and reduced haze infilms as compared to the Comparative Examples. Additionally, bothExamples have lower M_(w)/M_(n), ratios than Comparative Example 4. TheM_(z) is lower for the Examples in Table 6 in comparison to theComparative Examples. A lower value for M_(z), which is related to alower high molecular weight tails, is also known to be associated with alower haze value. Higher molecular weight gives higher melt strength andincreases the chance of surface roughness in film processing. Surfaceroughness is believed to negatively impact surface haze. The ratio ofthe absolute weight average molecular weight, M_(w,AbS), over theconventional weight average molecular weight, M_(w,GPC), as shown inTable 7 indicates that long chain branching exists in all the Examplesand four Comparative Examples as the value is greater than one.

A linear polymer would give a gpcBR value expected to be at or nearzero. Typically as the level of long chain branching increases the gpcBRindex value increases, from the value of zero. As can be seen by thebranching information in Table 8, the Examples show slightly less longchain branching than their related Comparative Examples. This would beexpected given that high molecular weight material is suppressed earlyon in the formation of the Examples but not in the Comparative Examples.

The results of DSC analysis using the DSC method for Examples 1 and 2and Comparative Examples 1-4 are reported in Table 9.

TABLE 9 DSC data for Examples and Comparative Examples 1-4. Heat ofT_(m) Fusion % Density Sample (° C.) (J/g) Cryst. T_(c) (° C.) (g/cm³)Example 1 112.3 151.7 52.0 100.8 0.925 Comparative Example 1 113.0 150.651.6 100.6 0.925 Example 2 112.0 151.2 51.8 100.1 0.924 ComparativeExample 2 112.2 151.6 51.9 100.4 0.925 Comparative Example 3 113.1 148.650.9 100.7 0.925 Comparative Example 4 111.5 149.2 51.1 99.5 0.923

For a given density, the two Example samples generally have a higherheat of fusion as compared to the Comparative Examples.

The results of the sulfur analysis using the Total Sulfur Concentrationmethod for Examples 1 and 2 and Comparative Examples 1 and 2 arereported in Table 10.

TABLE 10 XRF detected sulfur concentration in the ethylene-based polymersamples Examples 1 and 2 and Comparative Examples 1 and 2. XRF measuredS concentration ppm Sample (by weight) Example 1 143 Comparative Example1 0 Example 2 147 Comparative Example 2 0

The XRF analysis of Examples 1 and 2 show the sulfur concentration valueas a result of the sulfur containing high-Cs chain transfer agentcompound (in this case, TDM) used in the production of Example 1 and 2.Since no sulfur-containing CTA is used for Comparative Examples 1 and 2,no sulfur is expected in those samples and none is found.

The zero shear viscosity, η₀, analysis is reported for the two Examples,the analogous Comparative Examples, and several commercially availableComparative Examples in Table 11. In order to better observe therelationship, the factor called “Zg” is defined as the log zero shearviscosity multiplied by the ratio of the conventional weight averagemolecular weight to the absolute weight average molecular weight asshown in Equation 12:Zg=Log η₀*(M _(w,GPC) /M _(w,Abs))  (Eq. 12)

TABLE 11 Density, melt index, weight average molecular weight (GPC andAbsolute and their log values), zero shear viscosity and its log value,and the Zg ratio for the Examples and Comparative Examples. Zg = Logη_(o) Log Log η_(o) * Density M_(w, GPC) M_(w,Abs) 190° C. (M_(w.GPC)(M_(w,Abs) (M_(w,GPC)/ Sample (g/cc) I₂ (g/10 min) (g/mol) (g/mol) (Pa ·s) (g/mol)) (g/mol)) M_(w.Abs)) Example 1 0.925 1.10 79,330 119,74012,830 4.90 5.08 2.72 Example 2 0.924 1.08 81,820 127,270 13,630 4.915.10 2.65 CE 1 0.925 1.13 81,400 121,630 14,540 4.91 5.09 2.79 CE 20.925 1.11 85,190 129,030 14,940 4.93 5.11 2.76 CE 3 0.925 1.04 80,960122,220 16,150 4.91 5.09 2.79 CE 4 0.923 0.82 97,560 155,070 24,160 4.995.19 2.76 CE 5 0.928 0.37 100,680 219,740 46,130 5.00 5.34 2.14 CE 60.923 0.78 84,440 171,110 15,590 4.93 5.23 2.07 CE 7 0.924 0.75 75,630124,140 15,460 4.88 5.09 2.55 CE 8 0.927 0.70 103,690 208,620 31,8905.02 5.32 2.24 CE 9 0.933 0.63 98,450 195,770 35,550 4.99 5.29 2.29 CE10 0.928 0.64 92,940 166,120 34,620 4.97 5.22 2.54 CE 11 0.927 0.47103,090 190,350 49,390 5.01 5.28 2.54 CE 12 0.920 0.15 142,110 370,280189,086 5.15 5.57 2.03 CE 13 0.922 2.48 85,380 184,570 6,364 4.93 5.271.76 CE 14 0.919 0.39 124,830 348,570 59,307 5.10 5.54 1.71 CE 15 0.9220.80 92,150 198,980 21,766 4.96 5.30 2.01 CE 16 0.916 28.49 76,140184,120 469 4.88 5.27 1.10 CE 17 0.917 6.40 101,880 289,980 2,604 5.015.46 1.20 CE 18 0.924 1.76 82,500 175,320 9,249 4.92 5.24 1.87 CE 190.926 5.61 64,600 173,180 2,878 4.81 5.24 1.29 CE 20 0.923 0.26 128,410294,580 107,690 5.11 5.47 2.19 CE 21 0.924 0.22 129,140 287,180 189,0635.11 5.46 2.37 CE 22 0.924 0.81 104,040 222,980 29,021 5.02 5.35 2.08 CE23 0.926 5.85 71,030 153,990 2,915 4.85 5.19 1.60 CE 24 0.924 2.0188,900 190,140 9,082 4.95 5.28 1.85 CE 25 0.929 2.50 61,490 119,0005,813 4.79 5.08 1.95 CE 26 0.924 0.79 98,690 160,590 25,178 4.99 5.212.70 CE 27 0.922 0.25 130,310 236,910 126,928 5.11 5.37 2.81 CE 28 0.9243.41 77,990 125,750 4,479 4.89 5.10 2.26 CE 29 0.923 2.00 80,790 176,8808,176 4.91 5.25 1.79 CE 30 0.923 1.00 91,360 204,310 18,293 4.96 5.311.91 CE 31 0.925 1.82 80,440 205,500 8,825 4.91 5.31 1.54 CE 32 0.9230.81 93,110 236,090 24,085 4.97 5.37 1.73 CE 33 0.922 33.34 41,80082,220 273 4.62 4.91 1.24 CE 34 0.921 2.09 89,780 171,160 6,662 4.955.23 2.01 CE 35 0.922 0.67 89,040 168,820 20,012 4.95 5.23 2.27 CE 360.923 4.09 113,280 249,620 4,304 5.05 5.40 1.65 CE 37 0.918 0.46 259,820891,380 55,451 5.41 5.95 1.38 CE 38 0.912 200.00 68,130 186,700 58 4.835.27 0.64 CE 39 0.924 0.70 88,120 166,500 31,453 4.95 5.22 2.38 CE 400.918 7.89 145,200 419,340 1,881 5.16 5.62 1.13 CE 41 0.922 4.06 143,910348,180 4,249 5.16 5.54 1.50 CE 42 0.921 4.63 123,360 276,410 3,639 5.095.44 1.59 CE 43 0.919 6.76 129,320 313,570 2,408 5.11 5.50 1.39 CE 440.923 19.60 66,960 129,380 669 4.83 5.11 1.46 CE 45 0.928 0.60 103,930205,740 39,348 5.02 5.31 2.32 CE 46 0.931 3.20 71,630 146,670 4,607 4.865.17 1.79 Linear 0.953 1.04 118,530 115,000 7,830 5.07 5.06 4.01Standard 1The relationship between Zg and the absolute molecular weight is shownin FIG. 5. Due to the separation between the Examples and both theanalogous and commercially Comparative Examples, lines of demarcationbetween the groups to emphasize the difference may be established for agiven log absolute weight average molecular weight. As shown in FIG. 5,the following numerical relationship exists:(3.6607*Log M _(w,Abs))−16.47<Log η₀*(M _(w,GPC) /M_(w,Abs))<(3.6607*Log M _(w,Abs))−14.62.  (Eq. 13)

Although not shown in FIG. 5, the following numerical relationship alsoexists based upon the information in Table 11:(3.6607*Log M _(w,Abs))−16.47<Log η₀*(M _(w,GPC) /M_(w,Abs))<(3.6607*Log M _(w,Abs))−14.62  (Eq. 14)for log M_(w, Abs) values less than 5.23, and2.675<Log η₀*(M _(w,GPC) /M _(w,Abs))<(3.6607*Log M_(w,Abs))−14.62  (Eq. 15)for log M_(w, Abs) values equal to or greater than 5.23.

Examples 1 and 2, which are ethylene-based polymers, as shown in FIG. 5,further comprise sulfur.

Haze data is reported for films produced from both Examples, theanalogous Comparative Examples, and several commercially availableComparative Examples in Table 12. FIG. 6 shows a plot of the data givenin Table 12 for surface/internal haze versus melt index (I₂).

TABLE 12 Density, melt index, haze, internal haze, surface haze, andsurface/internal haze ratio for Examples 1 and 2, Comparative Examples1-4, and 47-82. Melt Surface/ Index (I₂) Internal Surface Internal (g/10Density Haze Haze Haze Haze Sample minutes) (g/cm³) (%) (%) (%) RatioExample 1 1.1 0.925 6.07 2.80 3.27 1.17 Example 2 1.1 0.924 6.08 2.963.12 1.05 Comparative 1.1 0.925 6.80 2.48 4.32 1.74 Example 1Comparative 1.1 0.925 6.81 2.58 4.23 1.64 Example 2 Comparative 1.10.925 6.92 2.82 4.10 1.45 Example 3 Comparative 0.82 0.923 8.53 2.006.53 3.27 Example 4 Comparative 0.63 0.926 7.23 1.79 5.43 3.03 Example47 Comparative 0.64 0.928 7.11 2.06 5.05 2.46 Example 48 Comparative0.47 0.927 7.57 1.68 5.89 3.51 Example 49 Comparative 0.37 0.928 6.061.92 4.13 2.15 Example 50 Comparative 0.69 0.923 9.63 1.65 7.98 4.84Example 51 Comparative 0.52 0.929 9.42 1.40 8.02 5.74 Example 52Comparative 1.7 0.924 6.40 1.91 4.49 2.35 Example 53 Comparative 0.890.924 7.38 1.81 5.57 3.07 Example 54 Comparative 2.1 0.918 16.94 1.5115.43 10.22 Example 55 Comparative 2.0 0.920 5.39 2.84 2.55 0.90 Example56 Comparative 0.73 0.920 6.24 2.18 4.06 1.86 Example 57 Comparative0.23 0.921 9.74 0.51 9.23 18.10 Example 58 Comparative 0.70 0.922 5.561.04 4.52 4.35 Example 59 Comparative 2.1 0.922 4.63 1.82 2.81 1.54Example 60 Comparative 0.26 0.919 12.72 0.53 12.19 23.00 Example 61Comparative 2.4 0.927 4.98 2.90 2.08 0.72 Example 62 Comparative 1.80.925 5.99 2.20 3.79 1.72 Example 63 Comparative 0.76 0.925 11.16 1.559.61 6.20 Example 64 Comparative 1.9 0.920 6.17 1.47 4.70 3.20 Example65 Comparative 0.83 0.921 4.80 1.13 3.67 3.25 Example 66 Comparative0.76 0.924 5.97 1.32 4.65 3.52 Example 67 Comparative 2.0 0.925 5.202.22 2.98 1.34 Example 68 Comparative 2.6 0.925 7.70 3.38 4.32 1.28Example 69 Comparative 0.30 0.917 12.09 0.36 11.73 32.58 Example 70Comparative 0.26 0.922 5.65 0.74 4.91 6.64 Example 71 Comparative 1.90.919 5.38 1.17 4.21 3.60 Example 72 Comparative 2.3 0.920 4.92 1.613.31 2.06 Example 73 Comparative 0.81 0.922 6.69 1.12 5.57 4.97 Example74 Comparative 0.73 0.924 6.88 1.42 5.46 3.85 Example 75 Comparative 1.90.924 4.49 2.07 2.42 1.17 Example 76 Comparative 2.1 0.921 5.36 1.513.85 2.55 Example 77 Comparative 2.3 0.931 6.77 3.21 3.56 1.11 Example78 Comparative 3.6 0.931 7.38 4.24 3.14 0.74 Example 79 Comparative 2.70.923 6.83 2.01 4.82 2.40 Example 80 Comparative 2.0 0.922 7.04 0.426.62 15.76 Example 81 Comparative 0.92 0.924 7.72 1.30 6.42 4.94 Example82

As defined in the Surface and Internal Haze method, described infra inthe Testing Methods section, surface haze is the difference betweenoverall haze and internal haze. As can be seen in Table 12, the Exampleshave a relatively lower surface/internal haze value compared to theanalogous Comparative Examples. These results show that by narrowing theM_(w)/M_(n), of the two Examples that the surface haze is reduced ascompared to the Comparative Examples with a similar melt index (I₂). Itis believed that the surface roughness of the films made from theExamples are reduced versus the Comparative Examples, thereby improvingthe surface haze value. The surface/internal haze ratio shows the effectof changes in surface haze on film properties to an extent normalizingfor density differences among the polymer products. The total haze ofthe Examples is reduced versus the Comparative Examples by reducing thesurface haze.

Using data from Table 12, a comparison plot is shown in FIG. 6 betweenthe surface haze, S, the internal haze, I, both in units of % and bothdetermined by using the Surface and Internal Haze method, and the meltindex (I₂). Due to the separation between the Examples and both theanalogous and commercially Comparative Examples, a line of demarcationbetween the two groups to emphasize the difference may be establishedfor a given melt index (I₂) range. As shown in FIG. 6, the followingnumerical relationship exists:S/I≦(−0.057*I ₂)+1.98  (Eq. 16)Although not shown in FIG. 6, the following numerical relationship alsoexists based upon the data in Table 12:S/I≦(−0.057*I ₂)+1.85  (Eq. 17)For the ethylene-based polymers described by both of theserelationships, the melt index (I₂) range may be from about 0.1 to about1.5. For these ethylene-based polymers, the polymers may furthercomprise sulfur.

The GPC-LS Characterization value, Y, is reported for the Examples, theanalogous Comparative Examples, and several commercially availableComparative Examples in Table 13. FIGS. 2 and 3, previously disclosed,show concentration-normalized LS chromatogram curves and GPC-LSCharacterization analysis for Example 1 and Comparative Example 4,respectively.

TABLE 13 GPC-LS Characterization for the Examples and both analogous andcommercially Comparative Examples (CE). Ratio of MI (I2) Density SampleA/B x Y (g/10 minutes) (g/cm3) Example 1 0.30 −10.9 3.3 1.1 0.925Example 2 0.23 −10.9 2.5 1.1 0.924 Comparative 0.20 −10.5 2.1 1.1 0.925Example 1 Comparative 0.15 −11.3 1.7 1.1 0.925 Example 2 Comparative0.20 −9.06 1.8 1.0 0.925 Example 3 Comparative −0.03 −8.66 −0.3 0.820.923 Example 4 Comparative 0.02 0.57 0.0 0.15 0.920 Example 83Comparative 0.26 0.19 −0.1 2.5 0.921 Example 84 Comparative 0.07 0.630.0 0.39 0.919 Example 85 Comparative 0.19 −0.14 0.0 0.80 0.923 Example86 Comparative 0.23 0.99 −0.2 29 0.916 Example 87 Comparative 0.18 0.96−0.2 6.4 0.917 Example 88 Comparative 0.35 0.41 −0.1 1.8 0.925 Example89 Comparative 0.34 0.94 −0.3 5.6 0.927 Example 90 Comparative 0.06 0.380.0 0.26 0.923 Example 91 Comparative −0.05 0.21 0.0 0.22 0.924 Example92 Comparative 0.06 −0.12 0.0 0.81 0.925 Example 93 Comparative 0.250.52 −0.1 5.9 0.927 Example 94 Comparative 0.17 0.09 0.0 2.0 0.925Example 95 Comparative −0.13 0.89 0.1 4.1 0.924 Example 96 Comparative0.34 1.20 −0.4 33 0.922 Example 97 Comparative −0.11 1.22 0.1 4.1 0.921Example 98 Comparative 0.13 1.51 −0.2 0.46 0.917 Example 99 Comparative−0.05 −0.99 0.0 2.1 0.920 Example 100 Comparative −0.26 0.18 0.0 2000.912 Example 101 Comparative −0.08 1.30 0.1 8.2 0.917 Example 102Comparative 0.04 −1.18 0.1 0.67 0.921 Example 103 Comparative −0.06−6.45 −0.4 0.79 0.923 Example 104 Comparative −0.24 −2.06 −0.5 0.250.921 Example 105 Comparative 0.09 −6.56 0.6 3.4 0.924 Example 106Comparative −0.16 0.81 0.1 4.6 0.920 Example 107 Comparative 0.37 0.92−0.3 1.8 0.925 Example 108 Comparative 0.28 0.68 −0.2 0.81 0.923 Example109 Comparative −0.13 1.06 0.1 6.8 0.919 Example 110 Comparative 0.16−1.51 0.2 1.9 0.924 Example 111 Comparative 0.27 0.44 −0.1 1.9 0.920Example 112 Comparative 0.31 −0.98 0.3 2.3 0.931 Example 113 Comparative0.21 0.35 −0.1 0.64 0.923 Example 114 Comparative 0.37 −0.15 0.1 1.80.925 Example 115 Comparative 0.36 0.16 −0.1 0.83 0.921 Example 116Comparative 0.10 0.08 0.0 0.23 0.921 Example 117 Comparative 0.44 1.13−0.5 2.0 0.925 Example 118 Comparative 0.13 0.18 0.0 0.21 0.922 Example119 Comparative 0.38 0.89 −0.3 2.7 0.923 Example 120 Comparative 0.080.19 0.0 0.30 0.917 Example 121 Comparative −0.13 0.33 0.0 0.16 0.921Example 122 Comparative 0.44 1.15 −0.5 2.6 0.925 Example 123 Comparative−0.01 −1.05 0.0 0.81 0.922 Example 124 Comparative 0.32 0.77 −0.2 2.00.922 Example 125 Comparative 0.00 0.22 0.0 2.0 0.921 Example 126Comparative 0.05 0.49 0.0 0.26 0.919 Example 127 Comparative 0.32 0.77−0.2 0.26 0.922 Example 128 Comparative 0.26 −0.35 0.1 0.91 0.924Example 129 Comparative 0.17 −0.25 0.0 0.70 0.922 Example 130Comparative 0.32 0.44 −0.1 2.3 0.923 Example 131 Comparative 0.24 0.27−0.1 0.92 0.924 Example 132 Comparative 0.42 1.03 −0.4 0.76 0.924Example 133 Comparative −0.01 1.22 0.0 2.4 0.918 Example 134 Comparative0.45 −0.79 0.4 3.6 0.931 Example 135 Comparative 0.25 0.10 0.0 2.2 0.927Example 136 Comparative 0.37 0.81 −0.3 2.7 0.923 Example 137 Comparative0.07 −1.18 0.1 0.76 0.925 Example 138 Comparative 0.24 0.03 0.0 2.10.922 Example 139 Comparative 0.14 0.03 0.0 1.9 0.919 Example 140Comparative 0.53 0.31 −0.2 2.4 0.927 Example 141 Comparative 0.37 0.85−0.3 2.7 0.923 Example 142 Comparative 0.30 0.49 −0.1 1.9 0.925 Example143 Comparative 0.08 −0.86 0.1 2.1 0.921 Example 144 Comparative 0.020.53 0.0 0.26 0.918 Example 145 Comparative 0.04 −1.69 0.1 0.73 0.924Example 146 Comparative 0.13 1.50 −0.2 0.43 0.919 Example 147Comparative 0.12 1.49 −0.2 0.48 0.918 Example 148 Comparative −0.01−0.60 0.0 0.71 0.924 Example 149 Comparative 0.04 1.32 0.0 2.2 0.918Example 150 Comparative 0.01 −1.36 0.0 2.4 0.920 Example 151 Comparative0.26 0.77 −0.2 2.0 0.922 Example 152 Comparative −0.10 1.20 0.1 7.90.919 Example 153 Comparative 0.27 0.89 −0.2 6.6 0.927 Example 154Comparative 0.34 0.65 −0.2 0.37 0.928 Example 155 Comparative −0.08 0.210.0 0.70 0.927 Example 156 Comparative −0.08 0.07 0.0 0.63 0.933 Example157 Comparative −0.05 −0.31 0.0 0.64 0.928 Example 158 Comparative −0.09−0.25 0.0 0.47 0.927 Example 159 Comparative 0.17 0.32 −0.1 0.92 0.921Example 160

As can be seen from the data presented in Table 13, none of theanalogous or commercially Comparative Examples have a GPC-LSCharacterization value that is greater than 2.1, whereas both Exampleshave a value greater than 2.1. The GPC-LS Characterization equationcaptures the effect of suppressing the molecular weight of the chainsformed early in the reactor with a high-Cs CTA, thereby narrowing themolecular weight distribution while still permitting some long chainbranching, which is indicative of low density polyethylene, to occur inthe later part of the process when a low-Cs CTA predominates. Thisresults in a product with a lower molecular weight in the “log MW valueof 6” molecular weight range (as can be seen in FIG. 2) and lower gpcBRvalues (as indicated in Table 8).

An extrusion multi-pass test is performed on Example 1 and ComparativeExample 3 to determine relative atmospheric stability of the inventivepolymer over the comparative polymer. A 5-pass test is used and isconducted per the Extrusion Multi-pass method, described infra in theTesting Methods section. Tables 14 and 15 show, respectively, theconditions of each pass for Example 1 and Comparative Example 3. FIG. 6shows the melt index (I₂) of Example 1 and Comparative Example 3 aftereach pass. Melt index, I₂, is tested on samples taken before thecampaign as well as on samples taken between each run.

TABLE 14 Feed and processing conditions for Example 1 during 5-passExtrusion Multi-pass test. Feed Rate Pass (lbs/hr) Melt Temp. (° C.)Torque (m - g) Die Press. (psi) 1 5.0 222 2700 520 2 4.5 223 2100 485 34.2 222 2000 475 4 4.3 222 1900 460 5 4.4 222 1900 465

TABLE 15 Feed and processing conditions for Comparative Example 3 during5-pass Extrusion Multi-pass test. Feed Rate Pass (lbs/hr) Melt Temp. (°C.) Torque (m - g) Die Press. (psi) 1 4.55 224 2700 490 2 3.95 226 2200460 3 4.6 221 2300 500 4 4.6 223 2300 500 5 4.7 222 2300 500As can be seen in FIG. 7, Comparative Example 3 shows significantly moreoxidative degradation than Example 1 for the near-analogous conditionsgiven in Tables 14 and 15. Comparative Example 3 has a 23.0% reductionin melt index (1.061 g/10 min. “as received” and 0.817 g/10 min. afterthe 5th pass) versus an 11.3% reduction in melt index (1.125 g/10 min“as received” and 0.998 g/10 min after the 5th pass) for Example 1.These data are also summarized in Table 15 for the melt index and alsofor the M_(w,GPC) in which a 7.65% change is seen for ComparativeExample 3 and only a 1.18% change for Example 1.

TABLE 16 Multiple pass extrusion data on Comparative Example 3 (CE 3)and Example 1 for 5 passes showing the melt index I₂ change and theweight average molecular weight change M_(w,GPC). I₂ % M_(w, GPC) %Change Change from As M_(w, GPC) from As Sample Pass I₂ (g/10 min)Received (g/mol) Received CE 3 As Received 1.06 86,510 CE 3 1st Pass1.01 −5.28 86,650 0.16 CE 3 2nd Pass 0.98 −8.04 87,960 1.68 CE 3 3rdPass 0.88 −17.18 89,320 3.25 CE 3 4th Pass 0.86 −19.01 92,070 6.43 CE 35th Pass 0.82 −23.03 93,130 7.65 Example 1 As Received 1.13 84,110Example 1 1st Pass 1.07 −4.53 82,900 −1.44 Example 1 2nd Pass 1.06 −5.9684,580 0.56 Example 1 3rd Pass 1.06 −5.96 83,690 −0.50 Example 1 4thPass 1.03 −8.62 84,530 0.50 Example 1 5th Pass 1.00 −11.29 85,100 1.18

Dynamic Mechanical Spectroscopy data were gathered and conducted usingthe Dynamic Mechanical Spectroscopy method described infra in theTesting Methods section. FIGS. 8, 9, and 10 show, respectively, theviscosity overlay, the tan delta overlay, and van Gurp-Palmen (Trinkle,S. and C. Friedrich, Rheologica Acta, 2001. 40(4): p. 322-328) analysisfor Examples 1 and 2 and Comparative Examples 1-4. These data aresummarized in Tables 17-19.

TABLE 17 Dynamic mechanical complex viscosity data at 190° C. of Example1-2 and Comparative Examples (CE) 1-4. Frequency Viscosity (Pa-s) at190° C. (rad/s) Example 1 CE 1 Example 2 CE 2 CE 3 CE 4 0.03 12,89914,679 13,804 15,803 15,620 23,182 0.04755 12,533 14,375 13,359 15,33915,172 21,795 0.07536 11,967 13,616 12,706 14,386 14,300 19,866 0.1194311,224 12,577 11,830 13,172 13,156 17,635 0.18929 10,323 11,358 10,80811,837 11,824 15,364 0.3 9,308 10,061 9,677 10,414 10,435 13,136 0.475478,227 8,744 8,503 9,018 9,040 11,082 0.75357 7,145 7,471 7,349 7,6677,700 9,203 1.19432 6,102 6,290 6,243 6,432 6,463 7,547 1.89287 5,1245,216 5,220 5,316 5,347 6,115 3 4,240 4,270 4,302 4,337 4,366 4,8994.75468 3,460 3,451 3,499 3,496 3,522 3,885 7.53566 2,789 2,759 2,8112,788 2,810 3,052 11.9432 2,221 2,182 2,232 2,200 2,219 2,377 18.92871,749 1,709 1,754 1,719 1,735 1,835 30 1,365 1,327 1,365 1,332 1,3451,407 47.5468 1,054 1,021 1,053 1,024 1,034 1,070 75.3566 808 780 805781 789 809 119.432 613 590 610 590 596 607 189.287 460 442 457 442 446450 300 335 321 332 320 324 325

TABLE 18 Tan Delta at 190° C. of Example 1-2 and Comparative Examples(CE) 1-4. Tan Delta at 190° C. Frequency (rad/s) Example 1 CE 1 Example2 CE 2 CE 3 CE 4 0.03 8.66 6.37 7.70 5.56 5.87 3.66 0.04755 6.20 4.645.65 4.27 4.38 2.94 0.07536 4.69 3.63 4.31 3.39 3.46 2.45 0.11943 3.672.93 3.41 2.78 2.82 2.10 0.18929 2.96 2.45 2.79 2.34 2.37 1.83 0.3 2.462.10 2.34 2.02 2.04 1.63 0.47547 2.10 1.83 2.00 1.77 1.79 1.46 0.753571.82 1.62 1.75 1.57 1.59 1.33 1.19432 1.61 1.45 1.55 1.42 1.43 1.221.89287 1.43 1.32 1.39 1.29 1.29 1.12 3 1.30 1.20 1.26 1.18 1.19 1.054.75468 1.18 1.11 1.16 1.09 1.09 0.98 7.53566 1.09 1.03 1.06 1.01 1.020.92 11.9432 1.01 0.96 0.99 0.95 0.95 0.86 18.9287 0.94 0.90 0.92 0.890.89 0.82 30 0.88 0.85 0.86 0.84 0.84 0.78 47.5468 0.83 0.80 0.81 0.790.80 0.74 75.3566 0.78 0.76 0.77 0.76 0.76 0.71 119.432 0.74 0.73 0.730.72 0.72 0.68 189.287 0.70 0.68 0.69 0.68 0.68 0.64 300 0.62 0.61 0.610.61 0.61 0.58

TABLE 19 Complex modulus (G*) in Pa and Phase Angle at 190° C. ofExample (Ex.) 1-2 and Comparative Examples (CE) 1-4. Ex. 1 CE 1 Ex. 2 CE2 CE 3 CE 4 Ex. 1 Phase CE 1 Phase Ex. 2 Phase CE 2 Phase CE 3 Phase CE4 Phase G* (Pa) Angle G* (Pa) Angle G* (Pa) Angle G* (Pa) Angle G* (Pa)Angle G* (Pa) Angle 387 83.41 440 81.08 414 82.60 474 79.80 469 80.33695 74.74 596 80.83 683 77.83 635 79.96 729 76.81 721 77.14 1,036 71.20902 77.96 1,026 74.58 958 76.94 1,084 73.54 1,078 73.87 1,497 67.781,341 74.75 1,502 71.16 1,413 73.67 1,573 70.20 1,571 70.49 2,106 64.511,954 71.36 2,150 67.83 2,046 70.26 2,241 66.87 2,238 67.15 2,908 61.372,792 67.91 3,018 64.51 2,903 66.85 3,124 63.63 3,131 63.88 3,941 58.433,912 64.54 4,158 61.37 4,043 63.49 4,288 60.52 4,298 60.76 5,269 55.675,384 61.27 5,630 58.32 5,538 60.31 5,777 57.57 5,803 57.75 6,935 53.077,288 58.12 7,512 55.49 7,456 57.24 7,682 54.78 7,719 54.96 9,014 50.649,698 55.13 9,874 52.78 9,880 54.31 10,062 52.13 10,120 52.29 11,57448.34 12,721 52.38 12,809 50.31 12,907 51.64 13,010 49.73 13,097 49.8614,698 46.26 16,452 49.78 16,410 47.98 16,635 49.12 16,624 47.45 16,74647.57 18,473 44.30 21,014 47.38 20,791 45.81 21,181 46.78 21,008 45.3521,175 45.45 23,002 42.48 26,525 45.15 26,064 43.81 26,662 44.61 26,27643.39 26,501 43.48 28,387 40.79 33,107 43.12 32,345 41.97 33,194 42.6332,542 41.60 32,836 41.68 34,742 39.25 40,937 41.24 39,804 40.29 40,95540.81 39,973 39.96 40,353 40.02 42,201 37.82 50,133 39.54 48,543 38.7550,045 39.16 48,678 38.46 49,156 38.51 50,883 36.52 60,897 37.98 58,76537.33 60,674 37.64 58,846 37.07 59,442 37.12 60,962 35.33 73,197 36.5170,484 36.00 72,841 36.21 70,491 35.77 71,226 35.81 72,441 34.19 87,05534.80 83,655 34.37 86,508 34.53 83,573 34.17 84,459 34.20 85,253 32.78100,374 31.70 96,297 31.42 99,619 31.46 96,132 31.24 97,151 31.26 97,41029.96

As shown in FIG. 8, the inventive samples show less shear thinning thando the comparative samples. This is a reflection of the narrowermolecular weight distribution. It is expected that these materials mayrun with slightly higher backpressures when producing film than theComparative Examples. On the other had, as a result of the narrowermolecular weight distribution, some film properties may be expected toimprove. In FIG. 9, the inventive samples show higher tan δ values thando the comparative samples over the entire measured frequency range. Thehigher tan delta values reflect a less elastic material again resultingfrom the narrower molecular weight distribution. Highly elasticity maybe expected to contribute to pressure drop during extrusion, so this mayaid in the processing of these material. In FIG. 10 the G* versus Phaseangle plot, the inventive samples also show higher phase angle at thesame G* value than do the comparative samples. These results indicatethat the inventive samples have shorter relaxation times and are lesselastic than the comparative samples, which could be caused by theirnarrower MWD. The shorter relaxation times may be advantageous in filmblowing, allowing the material to relax more rapidly than theComparative Examples and thus relieving stresses in the film before thefilm crystallizes.

Melt strength values for Example 1 and 2 as well as Comparative Examples1-4 are shown in Table 18. The tests are conducted using the MeltStrength method described infra in the Testing Methods section. The meltstrength of Example 1 and 2 are lower than that of their respectiveComparative Example 1 and 2, again due to their narrower molecularweight distribution as compared to the comparative sample.

TABLE 18 Melt strength as determined by the Melt Strength method forExamples 1 and 2 and Comparative Examples 1-4. I₂ Density Melt Sample(190° C.) (g/cm³) Strength (cN) Example 1 1.1 0.925 9.4 Example 2 1.10.924 10.2 Comparative Example 1 1.1 0.925 9.9 Comparative Example 2 1.10.925 11.0 Comparative Example 3 1.0 0.925 10.8 Comparative Example 40.82 0.923 16.5

All patents, test procedures, and other documents cited, includingpriority documents, are fully incorporated by reference to the extentsuch disclosure is not inconsistent with this invention and for alljurisdictions in which such incorporation is permitted.

What is claimed is:
 1. An ethylene-based polymer with a density fromabout 0.90 to about 0.94 in grams per cubic centimeter, a molecularweight distribution (M_(w)/M_(n),) from about 2 to about 30, a meltindex (I₂) from about 0.1 to about 50 grams per 10 minutes, and furthercomprising from about 5 to about 4000 parts per million by weight ofsulfur as determined using a Total Sulfur Concentration method and basedupon the total weight of the ethylene-based polymer, and wherein theethylene-based polymer is formed from a reaction mixture comprising a“sulfur containing compound” containing a -S- functional group, inaddition to carbon atoms substituted with hydrogen atoms, and where aportion of the hydrogen atoms may optionally be substituted by inertsubstituents or moieties.
 2. An ethylene-based polymer of claim 1,wherein the polymer has a gpcBR value greater than 0.05 as determined bya gpcBR Branching Index by 3D-GPC.
 3. The ethylene-based polymer ofclaim 1, wherein the polymer has a GPC-LS Characterization value (Y)from about 2.1 to about
 10. 4. A composition comprising theethylene-based polymer of claim
 1. 5. The composition of claim 4,further comprising a polyolefin.
 6. An article comprising at least onecomponent formed from the composition of claim
 4. 7. The article ofclaim 6, wherein the article is selected from a film, an extrusioncoating, a molded article, a wire and cable coating, a crosslinkedarticle, or a foam.